SCIENTIFIC ABSTRACT MOROZ, L. M. - MOROZ, L. S.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001135210009-9
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: July 13, 2001
• Sequence Number: 9
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

The first prize of 10,000 roubles(imni Do K. Chernov) was awarded to the
following teams Professor So Z. Bokshteyn, Engineer To I. Gudkova, Doctor of
Technical Sciences Professor A* As Zhukhovitskly, Doctor of Technical Sciences
Profesvor So To Kishkin and Engineer L. M. Moroz for the paper "Investigation
of the diffusion and'the distribution of components in a real meta:1 by means of
radioactive tracers"* The work described IA this paper represents experimental
and the&r-ectical-w--ork of fundamental importance on diffusion in alloys as a func-
tion of the structure of the metal and the stress field caused by external action.
A brief summary is given of this paper and it is stated-,that it is not only of
major theoretical importance but also of practical interest, particularly from the
point of view of the problem of high temperature strength.
Results of the 1958 Competition for Obtaining imeni D. K. Chernov and Imeni
N. A. Mnkevich Prizes, Metallovedeniye i termicheskaya obrabotka metallov,
1959, No. 6, pp 62-64

85379
g.
AUTHORS:
S/032/60/0e,-6/C 10/007/035
7:0.0 1 6/'BO-4
TITLE:
Bokshteyn, S. Z., Gubareva, M. A., Kishkin, S. T., and
moroz, L. Ni.
Study of the Process of Iron R llization by the Method
of Radioactive Isotopes Iq
PERIODICAL: Zavodskaya labor-atoriya, 1~)60, Vol. 26, No. 10, pi~. '1'!-i1'4
TEXT: The authors studied the behavior of atoms at the grain boundaries
during the recrys tall izat ion of" iron (content in 0.021 C, 0-014 ?,
0.011 s, o.67 Si, 0.07 Al. 0.08 Kn, m6 Ni, o.o~~3 cu). Sam~;les of this
iron were covered with Fe59. In annealing, Fe59 spread due to diffusion
at the boundaries between the metal grains. This permitted an observati,~n
of the local displacement of atoms lying at the boundary during
deformation and recrystallization annealing. Iron rods were annealed at
12500C for 8 h, and then cut into samples ('0 xl0v,20 mm). The riveted
layer (70-80g) was removed by elentropolishing in perchloric anti j.-Jacial
acetic acids. An Fe59 layer 1.0 p thick was electrolytically to
Card 1/3

85379
Study of the ?rocess of Iron /O32/60/fO'-'
Recrystallization by the I'llethod of 30 16 / L_
Radioactive Isotopes
the polished surface. Subsequently, the samples were deformel by
compression by 10-16~o (Fig. 4'; an-3 by 45-70" (Fi,. 2). Fi6s. 1 -,, j"'inw the
/0
autoradiogram (a) on the left., anJ the microstructure kb) c'n the ri,:-..rit
on microphotographs. During exposure the gamples were prote-te-A ~1 f4-17D
1 p thick (1% of Zapon varnisn in the solvent PAJ) (RDV)). a'c produ-e the
autoradiograms, the samples were exposed for several days on ~,hotorraphi---
plates or films HWV,~A (NIKFI), type MP(MB). The autoradio,--rams were
compared with the microstructure pictures which had been taken by a
microscope of the type HOM-8 (MIY---8). Next, the recrystallization
annealing was carried out (Figs. 1; 5-8). A Table on P. 1115 rives the
hardness and the methods of treatment for scme samples. Or: the basis of
their methods, the authors succeeded in observin-r the behavior of brain
boundaries during plastic defcrmaticn and subsequent recrystallization.
It was proved that iron recrystallization at relatively low (11,.%') and high
(50-70%) degrees of deformation causes no essential change in the PCsition
of atoms laying at the boundary of deform,,d grains. With a considerable
structural change of the metal after -i double recrystallizatic,n. as well as
Card 2/3

85379
Study of the ?rocess ---f Iran S/O 32/60/026j"J- 7/
Recrystallization by tLe Method of B-016/B054
Radioactive Isotopes
after polymorphous a , y transformation, the atoms at the boundaries Cf
the initial bodies are not displaced. 'In contr-,st with recry-s tall izat ion.
plastic deformation i4j accompanied by a cinsiderable displacement of a,:-I,s,
The results prove that the displacement of grain boundaries during
recryntallization and the -jub:jequent growth of grains iii connected -Nith 11
specific mechanism which differs from the ordinary diffusion mechanism.
There are 8 figures, 1 table, ard 1~ references: 4 Soviet, 1 US, 1 Dutch,
1 French, and 4 German.
Card 3/3

S/129/61/000/001/002/013
Elll/E135
AUTHORS: Bokshteyn, S.Z.v Doctor of Technical Sciencesq?rofessor;
Gubareva, M.A., Engineer; Kontorovich, I.Ye., Doctor
of Technical Sciences; a
Technical Sciences pq_For-oz,,_kM. I Candidate of
TITLE: Peculiarities of the Diffusion of Carbon in 7ron
PERIODICAL: Metallovedeniye i termicheskaya obrabotka metallov,
1961, No. 1, pp. 10-14 (+ 1 plate)
TEXT; Work by two of the authors (Refs 1-4) and by others
(e.g. Refs 2, 3) has shown that diffusion is often non-uniform.
This effect could be associated with difference in the activation
energy of diffusion (Refs 8-10). In this present work the authors
studied diffusion of carbon in technical purity iron (0.0375' C) and
iron alloys with 0-03Z C and 0.11+, 0.61+ or 2-93..~' Si. some alloys
also contained a third component: 4-.56 or 3 Nis 0.36 or 1.61% Alt
0.88 1 3.77 or 14-13% Cr, 0.21 or 3% Mo, 1.19 or 4.97-'-' W, 0.1 or
2.29% Ti. This enabled the influence of carbide-forming and non-
forming elements to be compared. Pr smatic s0ecimens 2U mm high
and with a 10 mm base were used. Cl~ was depo'sited on the surface
Card 1/5

S/129/61/ooo/001/002/013
Elll/E13 5
Peculiarities of the Diffusion of Carbon in Iron
from barium carbonate or from special specimens containing this
isotope. The first technique was used for studies in the gamma, t
second In the alpha states. Auto-radiographs were obtained on he
type MAK~V (NTKFI) plates, contact prints being examined micro-
photometrically with a type MO-4 M-4) instrument. The diffusion
coefficient was calculated by the method of Bokshteyn et al (Ref.11).
Microstructural analysis was also carried out. Autoradiographs and
microstructures for iron at 950 OC are shown in FIg.la and b.
Autoradiographs at 550 'C for alpha iron (unalloyed and with o.64%
Sit top and bottom, respectively) are shown in Fig.2a and b.
Fig.5 shows plots of darkening, against depth of diffusion of carbon
in the grains (top curve) and alnn7 boundiriei (bottom curve In each
of the two diagrams), for ferrite k550 0--). The influence of
Concentration of the differont ailoYing ele-onts on depth of
diffusion (mm) in irnn at 95,~ cC i- ~;hnwn In Flg.6.
Card 2/ 5

S/129/6]L/000/001/002/013
H111/H135
Peculiarities of the Diffusion of Carbon in Iron
M. ~Al
Jep 0
71
If$ 4 8 17 is ox-1044M Cr
O.J.
it 7
L Ali
-9
0 so 170 ISO zwxlw'cm

Fig. Fig. 6
Card
.3/5

S/129/61/000/001/002/013
xll:L/El3 5
Peculiarities of the Diffusion of Carbon in Iron
Fig-7 shows.relative darkening with respect to distance into ferrite
grdin for carbide forming (left-hand graph) and non-forming (right-
hand graph) alloying elements. The left and right ends of the plots
re
late to the grain boundaries; the remaining spaceg corresponding
to 0.30 mm, relates to the body of the grain.
A-
Saw A.-
I'l ru
0
0
%
1,17% w
%
9,J
Fe
Fe
Card 1+15 #.w O.Ze A. X tiff Fig.7 Vo. 9.19 0.19

S/129/61/000/001/002/013
E111/9135
Peculiarities of the Diffusion of Carbon in Iron
The work shows that carbon diffusion in both alpha- and gamma-iron
occurs unevenly, the grain boundaries and adjacent alpha solid-
solution regions becoming enriched with carbon. The diffusion
coefficient for grain boundaries is 3-1+ orders higher than for
inside grains. Alloying modifies both rate of diffusion and
distribution of carbon within the grain; depending on the effect
of the element on the gamma region. Alloying reduces the
carbon-concentration drop between the boundary and the body of
the ferrite grain.
There are 7 figures and 11 references: 7 Soviet and 1+ non-Soviet.
Gard 5/5

BOKSHTEYN, S.Z. (Moskva); KISHKIN, S.T. (Moskva); LOZINSKIY, M.G. (Moskva);
SOKOLKOV, Ye.N. (Moskva); Prinimnli tichastlye: PODVCYSFAfA, O.N.;
ZILOVA, T.Y..; SOROKINA, K.P.; POLYk,, E.V.; MURCIZ, L.N.;
BULYGIN, I.F.; LASffAO, N.F.; POKUESTOVA, Ir.N.; 5GADEF--YETA, I.A.;
YAGLOV, R.V.; VOLODINA, T.A.; KORABL-VA, G.N.; ANTIFOVA, fe.l.
Thermomechanical treatment of chromium-nickel-manganese
austenitic steel. Izv. AN SSSR. Otd. tekh. nauk. Met. i topl.
no.2:15-21 Mr-Ap 162. (MIRA 15:4)
(Chromium-nickel steel--linrdening)

'00 -55
AUTHOP3 Boksht eyn 3 Z , Doc tor of 1'echnical ~~c i etic e-
Professor Ki shkin . 6,T,, , Corr rs pondi riv Membor )I iio
Academv of Sciences and '-Ioroz L (:,111didate C'I
Technical Sciences
i IT 1. E Influence of* carbon on the movr~mont L)l -zratn
boundaries in the re crystallization of iron
PERIODICAL Metallo vedenlye 1 termicheskaya obiabolka metal1k),
no, 3 196 2, 8 - 13
T i,XT LfAcke and Detert (Ref'.. I - Acta Metalturg v.. 5 no 11
195 7 ) and Beck (Ref. 2 - Metal Interfaces C I ev e I and A~i,%l 19 5 2
consider that there is a sharp drop in the speed of recry9talli -
zation when the concentration of an impurity reaches some
critical value iabout 0.0100 below the solubility. Impuritie5
forming a second phase also retard the growth of' recrystallization
centres,, Using their radioact ive- isotopes technique (i?f~t. 6-
"Zavodskaya laboratoriya. no. 10, 1960) the present author5 and
N1
. ..A, Gubareva have studied the influence of carbon on the
behaviour of grain boundaries in the recrystallization nt
Card I-A

VI
Int'lu-nce of carbon on t1Ll/F)-)5
t ec tin ic a I - gr iid c- i rLn - C a r b o n i% a -3 c 11 os c- n a S a n e I t-m --rj t
pr a(, t i c a I I y 1 nzn o I ub I e i n a I pha - i r on I [ 1~, KJIC,1~11 I o I v, I
a n L t I c r c a 5 e i n r h e Ac t i va i i on en orgy o t r oc 1 1, ~ I it I1 11,11 I'M C',
i r on a nd , i I p r e ~3 e n t i n (I u it I] t I ( I es ev ('11 --i I I gil I v 1 11 #-xC r-S ('t
solubii1tv to PrOVent c of I t-.c t Lve recryst all izat j tm 1) ZA I i I (. k I
lariv at ~1;0 - 7 () u OC ~ :m(,c impnz: were' sat ur cAt e J ~~ L t n' c iir h on
from donors at -1 0() OC t o r 2 tiou r -i The helia-lour o I ( arbon
atom~i at iron-gra in boundari es was f o1 lovied di rec t I y d i i r 1 11
deformat ion and subsequent recrystal I izing anneal ing
g
Recrystall ization wag StUdl ed on qpf-c imens 10 15 and 7)u
del ormed t iie f ir st beinQ i n I ac t c I oF v t o t hf, r i ti va I u r
Autoradiograms obtained belor t- and a ft t-r d t-f oi am t i on III' f. , ();,I
par ed From t h i s and t lie m ic ro-3 t ru( t Ul-e ~ he hPhaV L 011t 0 1 t h f-
c ~i rhon %,as eva I uat ed - I'lle sizes of all gr,iiri- Inc 1 ot--, ~! ' rr
deformation. heating to 550 OC lailed to rocr%-t.il
lization but grourth of alpha-phase grains occiiired I h(111
tended to move toward5 grain boundaries even then t h i mf-i ill
going int o it region of hi ~,hor ( orhou conc ent I ~t ion -1 !~ 'k,
r e1. r %-sral I izat ion was a lmost Comp] el t- t 1) 0 L ~ I I holl I f-Mil 1 11 1 H V .1!
~-ard 2A

Int-1 ueric e of carbon on El 1 ]/E7,55
the g-,-airi boundaries produced after heatint,,, ot -)')u0C-
Althoii,zh recrystailization was pract icall,, in~iojiton(-oil,,
-,)Mplotelv new fine-grained structure was product,d 0"I t I r1 Q t
)U C produced growth of recrystallized griins in~! mnvmnen!
not always. complete , of carbon to the new gri-st n hoiiivior i t--
decrystallLZation anneiling at 700 C for If5 111111 ot lmon,
after 131. deformation gave little change L11 micro~t I 'L~- tilt (,
carbon moved from the boundaries of deformed graiti!~ tk) those
of the neti;- recryEtallized grains. The -int'luence of' the alpha-
gamma transformation on the behaviour of carbon jtom-s loc,ttfd
a t ex r, o r i rii eri i
bourtdari es was studied in another series of
For this purpose specimens vc-re heated at 950 0(. fo'r I hour
Completely new grains were produced, the carbon both migrating
to them and forming large accumulations of carbides. It 1~;
e-ident that the behaviour Of LM[)U1-1ty atoms located at
bOUndilries and forming i.nterstitial sOlUtLO11S Is vorv different
from that of boundarv atoms of' the base element. as shown
previou:ily (Pef,. 6), boundary acoms in iron recr,,-StallizatLon
k~ard

-VI -
I r, I I 'A v I I c (- ~, I carbon on . ~ . . I., I I I / F,-; -~ 5
( c r 1, o i ,, m (, r ph 1 c t ra n!~, f o r ma tion) i emain in 1, III\- III,
9 a rii e p C) ~ 1 t 1 0 ri ,carbon atoins fol lot. new I %-- I orm(~d v r 1 1 n
b o u n (l a r -i e s .
f 11 t- r - i r- c () I i ~! 11 r es a ri d I t , i ii I r. .
,-arci ;[/-'I .x

9/129/62/000/009/001/006
E071/E492
AUTHOPS Bokshteyn, S.Z., Doctor of Technical S.ciences,Professor,
Bronfin, Engineer, Kishkin, S.T., Doctor of
Technical Sciences, Professor, Moroz, L.M., Candidate
of Technical Sciences
TITLE: Grain boundaries on recrystallization
PERIODIC\:,: Metallovedeniye i.termicheskaya obrabotka metallov,
no.9, 1962, 6-8
TEXT: This is a continuation of earlier work ("Zavodskaya
laboratoriya", no.10, 1960). The behaviour of W, Ni, Sn and
C admixtures present at the grain boundaries dur 'ing recr-ystallization
of iron (().021'. C, 0.01,4~~' P, 0.011-6 s, o,670, Si, 0.07',, AI,
U.08% Mn, o.0600' Ni, 0.033*,, Cu) was studied by autoradiogranhic
investigation and microstructural analysis. The admixture S,
forming with iron substitutional solid solutions in the case of
W, Ni, Sn and interstitial solid solutions in the case of C,
were in 'troduced by diffusion saturation at 600 to 7000C. The
recrystallization was carried out after preliminary deformations
of 10 to 15 and 50 to 70%. The Ni, W and Sn were completely
Card 1/3

S/I 29/62/000/009/001 /006
Grain boundaries ... E071/r,492
soluble in iron at all recrystal-lization temperatures
investigated and remained in their original lattice positions,
despite substantial changes in the structure of the metal.
The behaviour of carbon a toms wits SUbstantia I ly clif feren t :
above 7500C carbon passed from the boundaries of deformed grains;
to the boundaries of new recrystallized grains. However, in the
.L
initial stages of recrystallization (after 30 to 45 min at
650 to 750 aC) carbon atoms remain at the boundaries of t!i,
grains and boundaries of the new grains remain free from carbo:1.
The possibility of "heredity", i.e. preservation of the inLLi.ll
5tructuraL and concentration non-uniformities in recrysta'117f-O
metal was demonstra ted on a molybdenum alloy (0. 54% Zr, 0. `0
0.0008", Ti and 0.011'~ C). A thin layer of tungsten 185
electrodeposited on the surface of a flat specimen of the
alloy, submitted to a preliminary annealing at 17000C. 111c.
activated specimen was then annealed in vacuo at 17500C for'
100 hours. Autoradiographs of an oblique section showed the
presence of an accelerated diffusion not only along the botinc!aries
of the newly formed grains but also a preferential penetraLi~-i oL'
Card 2/3

S/129/62/000/009/001/006
Grain bo6ndaries ... E071/E492
the W185 along those sections where old grain boundaries. wore
passing be."ore recrystallization. The velocity of diffusion
along the old boundaries was lower than along the new boundaries,
nevertheless it was noticeably faster than.volume diffusion.
The results confirmed that within the grains the process of grain
boundary mi-gration does not pro-duce as high concentration of
, and at the end of the
defects as is produced at the"beginning
boun&%x-y migration. There are 6 figures.
Card 3/3

BOKSATEYN, S.Z.; KISHKIN, S.T.j HIKISHGV, A.S.1 POLYAK, E.11.1 SOLOVIYEVA, G.G.;
Prinimali uchastiyes ARWAKOV, V.M.1 BULANOV, A.V.; VERTYUKOVA, L,G.1
KORABLEVAj 14IRSKIY, L.M.; PODVOY3KAYA, O.N.; SAZONOOVA, 7,N.;
SOLONINA, O.P.j TITARENKO, I.I.; RINK, L.P.; KDZLOVA, M.N.;
YERMOLOVA, M.I.; ~C.ROZ L~~M.
Aging of plastically deformed alloys, Metalloved. i term. obr.
met. no.5340-" MY 163. (MIRA 16-5)
(Heat-resistant alloys-Hardening) (Deformations (Mechanics))

ACCESSION NR: AT4013954 S/L659/63/010/000/0214/0218
AUTHOR: Bokshteyn, S. Z Kishldn, S. T. ; Moroz, L. M.
77TLE: Condition of grain boundaries during recrystallization
SOURCE: AN SSSR. Institut metallurgii. Issledovaniya po zharoprochny*m splavam,
v. 10, 1963, 214-218
TOPIC TAGS: metal fatigue, steel grain, recrystallization, grain boundary
ABSTRACT- The present investigation dealt wit1i two problems: First, whether or not the
atoms of the initial grain boundary serve as the boundary of the newly-crystallized grains
and second, whether or not the initial grains leave traces of their inadequate structure, I. e.
whether their inadequacies are completely eliminated during recrystallization. Radioactive
isotopes were used for the Investigation of the grain boundaries during recrystaUization of
molybdenum, nickel, iron and Iron containing various impurities. The results showed that
the atom a of the base metal grain boundary do not take part in creating the grain boundaries
of the recrystallized metal and that the boundaries of the recrystallized grains inherit some
of the structural features of the initial grain. Orig. art- has: 3 figures.
ASSOCIATION: Institat metallurgil AN SSSR (Institute of Metallurgy AN SSSR)
Caw

ACCESSION N11: AT4040411 S/0000/G4/000/000/0074/0094
AUIT11011: Bokshtcyn, S. Z. ; Kishkin, S. T. ; Moroz, L. N1.
TITLE- investigation of the conditions of the grain boundaries during recrystallization of
iron and its alloys
SOURCE: Protsessy* diffuzii, struktura i svoysl-va mettallov (Diffusion processes,
structure and properties of metals); sbornik statey. Moscow, Izd-vo Mashinostroyeniye,
1964, 74-94
TOPIC TAGS: iron, iron alloy, steel, tungsten steel, carbon steel, steel structure,
grain boundary, recrys tall ization, iron microstructure, carbon diffusion, tungsten
diffusion, tin diffusion, nickel diffusion
ABSTRACT: There are still unclear aspects of the mechanism of recrystallization,
such as the nature of the reconstruction of grain boundaries, the formation of ne%v grains
and their Subsequent growth, the influence of impurities, and the role of diffusion. The
present authors investigated recrys tall ization of iron in specimens previously subjected to
a plastic deformation of 10-16 and 45-70%, involving a variety of heat treatments (anneal-
ing at 720--800C, recrystallization at 700-1370C, additional heating at 700-950C). Data
on microhardness before and after these processes are tabulated. Furthermore, recry-
Lrd 1 /4

ACCESSION NR: AT4040411
stallization was investigated on specimens of iron in which impurities were located at the
iron grain boundaries, formed a part of the solid solution by replacement or formed a
part of the solid solution by penetration; here again, various degrees of plastic deforma-
tion and various heat treatments were applied. The impurities tested were carbon, tin,
tungsten and nickel. Finally, radioactive isotopes were used as tracers to observe local
displacements of atoms by radio autographs, as well as by photomicrographs and X-ray
radiographs. In order to study the behavior of base-metal atoms, the isotope Fc59 was
used; for the behavior of atoms of a.- alloying elements, a corresponding isotope of the
alloying element was employed. Test specimens 10 x 10 x 20 mm were cut from iron bars
previously annealed (1250 C for 9 hrs. ) in order to obtain a homogeneous structure and a
coarser grain for the convenience of radiographic investigation. After cutting, the work-
hardened surface layer (70-80 microns) was removed by electrolytic polishing. The radio-
active tracer was deposited on the polished surface electrolytically. Diffusion annealing
was carried out in a vacuum furnace at residual pressures of 10-3 - 10-4 rrun Hg. The
temperature of diffusion annealing was 720C, at wMch the influence of grain boundaries on
the diffusional flux has been found to be particularly pronourced. Deformation of speci-
mens was carried out in a 200-ton Arnsler press. An analysis of the experimental results
showed that atoms of soluble impurities (nickel, tungsten, tin), like the atoms of the base-
2/4

ACC1'SSl`ON NR: AT40,10,111
sliov:ed that atoms of soluble impurities (nickel, tungsten. tin), like the atoms of the base-
meLal, practically remain at their initial locations despite significant changes in the micro-
s~ructurc of the metal. Prolonged annealing at recrystallization temperature (78 hrs. at
700C for iron with nickel; 30 hrs. for iron with tin; 28 hrs. at 750 C for iron with tungsten),
heatim, at temperatures above the A3-point, or high-temperature annealing (30 min. at
1200 C for iron with tungsten) did not cause atomic migration of impurities from the initial
locations toward the boundaries of the recrystallized grains, regardless of tile deuce of
prior deformation. During recrystallization, atoms of impurities which %%ere located at the
grain boundaries and formed part of the solid solution by penetration showed a substantially
different behavior than atoms of base-mctal at the boundaries or atoms of impurities form-
ing part of the solid solution by replacement. Carbon atoms, unlike atoms of iron, tungsten,
nickel, and tin, follow behind the boundaries of newly forming grains, so that at certain
stages of the process a lag -may occur due to a difference between the diffusion velocity of
carbon and the recrystallization velocity. It is characteristic that carbon atoms always
migrate toward the grain boundaries, and not in the direction of the maximum concentration
gradient of the impurity. The authors suggest, in conclusion, that the activation energy of
tile migration process be determined and compared with the activation energy of the dif-
fusion process of carbon in iron. Orig. art. has; 25 photomicrographs and 3 tables.
ASSOMATION: None
Lrd 3/4
L - -

ACCESSION NR: AT4040413 S/0000/64/000/000/OQ99/0109
AUTHOR: Bokshteyn, S. Z; Kishkin, S. T.; Moroz. L-M.; Chaply*gina. V. S.
TITLE: Structure imperfections of metal following recrystallization
SOURCE: Protsessy* diffuzii, struktura I svoystva metallov (Diffusion processes,
structure and properties of metals); abornik statcy. Moscow, lzd-vo Mashinostroyeniye,
'1964, 99-109
TOPIC TAGS: metal structure, metal diffusion, diffusion permeability, metal re-
crystallization, iron, tia, tungsten, carbon diffusion
ABSTRACT: Many of the properties and processes occurring in metals depend upon the
degree of structural perfection. However, it is not clear how and under what circum-
stances structural defects arise or disappear. In some cases, it has been possible to
act,ieve a displacement of interstitial impurities into the inner regions of grains by re-
crystallization, thus increasing the plasticity of the alloys. However, such a beneficial
Influence of recrystallization has been observed only in individual cases. Therefore, the
assumption can be made that in regions where grain boundaries have been located before
recrystallization, preservation of the specific state Is possible, I.e., there is a possibility
C. 1/3

ACCESSION NR: AT4040413
of "heredity". In the present'paper, the authors investigated the heredity of metal struc-
ture during recrystallization and grain growth, using autoradiographic and microscopic
techniques. The degree of structural perfection was evaluated by diffusion permeability
of C14, a higher permeability corresponding to a more defective structure. Using.
specimens of pure iron and of iron containing diffusionally introduced interstitial additions,
such as tin and tungsten, the authors studied the stability and degree of defectiveness of
the original grain boundaries during recrystallization in relation to the degree of metal
purity and the recrystallization conditions. Iron was annealed at 1250C for 9 hrs. ,
electropolished and etched with 4% picric acid in ethanol to reveal the structure. Tin
and tungsten were added in a microfurnace at 700C. Recrystallization was then carried
out either at 650C for 45 min., at 700C for 30 min. or at 750C for I hr., followed by
heating at 600C for I hr. in the presence -)f radioactive carbon. Measurements of hardness
and C14 distribution demonstrated that diffusion is affected by recrystaffization temperature
and that the residual effects of previous cold working can remain after application of the
common types of recrystaWzation. The diffusional mobility of atoms was found to in-
crease during the process of recrystallization. Failure of alloys at high temperatures
generally proceeds along the grain boundaries, but sometimes it occurs transgranularly.
It is possible that, in the latter case, the alloy falls along the boundaries of original
2/3

ACCESSION NR: AT4040413
grains which were metal lographic ally undetectable. The question of the influence of
various impurities on the defectiveness of the original grain boundaries thus gains con-
siderable significance. It is very possible that inheritance of defectiveness is linked to a
considerable degree to the presence of impurities; therefore, the question arises of the
possibility of displacing the impurities from the boundaries to the inner region by re-
crystallization. The results of the present investigation permit the authors to assume that
the detrimental influence of Impurities can be reduced by applying suitable recrystallization
conditions. Orig. art. has.: 7 figures and I table.
ASSOCIATION: none
SUB.W=LTED: 09Dec63 DATE ACQ: 28May64 ENCL: 00
SUB CODE: MIM NO REF SOV: 002 OTHEFL- 000

ACCESSION NR: AT4040422 S/0000/64/000/000/0183/0187
AUTHOR: Bokshteyn, S. Z.; Kishkin, S. T.; Moroz, L. M.
TITLE: Effect of thermomechanical treatment on diffusion mobility
SOURCE: Protgessy* diffuzii. struktura i avoystva metallov
(Diffusion processeS, structure and properties of metals); abornik
statey. Moscow, Iza-vo Mashinostroyeniye, 1964, 183-187
TOPIC TAGS: thermomachanical treatment, diffusion mobility,
diffusion coefficient, fine structure, diffusion mobility determina-
~ion, thermomechanical treatment effect
ABSTRACT: The diffusion mobility of iron in austenitic steel E1481
and E1437B alloy were investigated after conventional heat treatment
and after thermomechanical treatment (THT). The parameters of the
latter treatment were: 1080C - temperature of deformation; 28Z
reduction; and 13.5 m/min - deformation rate. The diffusion mobility
was determined by the method of tagged atoms in combination with
microstructure analysis. The specimens were electrolytically coated
Lc--,d -_i 1- 3

ACCESSION NR: AT4040422
with a thin film of radioactive Fe59 and annealed in a vacuum
furnace at 800C for 150 hr. After annealing, the diffusion coef-
ficients were calculated for grain volume and grain boundaries.
Table I (see enclosure) presents the results obtained. Thus, TMT
changes not only the conditions of the grain boundaries but of the
grain bodies as well. The increase of diffusion mobility is pre-
served even after annealing at higher temperatures (temperature
of recrystallization). The increase of diffusion mobility produced
by TMT limits the applicability of this method for heat-resistant
alloys. TMT could be beneficial, however, for alloy working at
relatively low temperature. Ori;j. art. has: 4 figures and 2 tables.
ASSOCIATION: none
SUBMITTED: 09Dec63 ATD PRESS: 3072 ENCL: 01
SUB CODEz MM NO REF SOVz 001 OTHER: 00
Card 2 /3

ACCESSION NR: AT4040422
ENCLOSURE: 01
Table 1. Iron diffusion coefficients
D-10 cm /sec on grain boundaries Dgr
and in grain bodies Db of alloys E1437B
and E1481 at 800C
Conventional
heat treatment
TMT
Alloy
Dgr Db Dgr Db
E1481
E1437B

.62
0.87
4
.6
3
.5 2.8
1.7 -
11
Average diffusion -coefficient
E1481
E14-37BJ 1.4
1.0 3.0
1.3
Card 3/3

1, 071~2-67 EWT (m)/EWP-(t- --upta)
ACC NRi AP6027751 WN1 SOURCE CODE: UR/037O/66/ooo/oo4/Ql39/rji42
AUTHOR: Boksbteyn, S. Z. (Moscow); Kishkin, S. T. (Moscow); Moroz, L. M. ~Moscow);
Chaplygina, V.
ORG: None
0 /_3
TITLE: Characteristics of carbon diffusion in niobium
SOURCE: AN SSSR. Izvestiya. Metally, no. 4, 1966, 139-142
TOPIC TAGS:- carbon, niobium, metal diffusion
ABSTRACT: The naLure of carbon diffusion in niobium is studied as a function of struc-:
'ture and surface state. The specimens were melted in a vacuum arc furnace, forged and
heat treated at 20001C for 10 hours to produce a uniform structure and relieve inter-
-nal stresses. Carbon diffusion was studied by autoradiography combined with micro-
structural analysis. The niobium specimens were diffusion saturated with radioactive
carbon at 9000C for 2 hours. Three types of carbon diffusion measurement in the sur-
face layer were compared: 1. directly after stabilizing annealing in a vacuum at
20001C for 10 hours; 2. after stabilizing annealing and mechanical destruction of the
surface layer by polishing the specimens on glass with abrasive powders of v3xying
'granularity and by preparation of a microsection; 3. in the oxidized surface of a mi"
1crosection. It was found that considerable diffusion of carbon tales place along the
Card 1/2 UDC: 548-526

L 07182-67
ACC NR: AP6027751 0
'grain boundaries of the niobium regardless of the state of the surface layer. The
.surface state has a considerable effect on volumetric diffusion. Annealed specimens
ishow practically no volumetric diffusion while specimens with a polished surface show I
considerable mobility of carbon atoms within the niobium grains. This diffusion is
!considerably stronger along the subgrain boundaries than in the remainder of the grain I
.volume. Analysis of the experimental results shows that carbon diffusion in niobium
:consists of three elementary processes: 1. diffusion of carbon in the crystal lattice
of niobium; 2. reactive diffusion with the formation of a carbide phase; 3. diffusion
of carbon in niobium carbides. The carbide phase is formed chiefly in defect sections
lof the structure: along the boundaries of grains and subgrains and also in the less
perfect sections of the grain volume where diffusion is most irtense. Orig. art. has:
l table.
!
/1 0
SUB CODE: Yk~ 7/SUBM DATE: OqMar65/ ORIG REF: 006/ OTH REF: 005
I_qcrd 2/2

ACCE&SION NR: AT4040404 S/0000/64/000/000/0015/0024
AUTHOR: Gubareva, M.A.; Moroz, L. M.
TITLE: A study of self diffusion and diffusion in nickel alloys
t)O~MCE: Protsessy* diffuz1f, struktura i svoystva metallov (Diffuc-ion prolesses, structure
and properties of inetals); sbornik statey. '114osc,)w, Izd-vo Nlashinos,royen.yt-~, 1964, 15-24
TOPIC TAGS: nickt,!, nickel alloy, Kli'.IONSOT", alloy, ZhS3 alloy, nickel selt diffusion,
bounda-ry rliffuF~inn, bulk diffu:,ior, iuLuradiogr%j,:ji,-, diffusion arialysis, self diffusion co-
efficien't, diffw;ion activation onergy, tin, tin diffusion
ABS"1"1U%CT: 'rhe authorii presen" a (101'a;led of diagram's f 'hr-
Nsii,ii in nickell and offer some cluilitauve eva1LJ,'tL1(j1-iS of 'Lho diffusif)il of Lin and self-diffusion
of nickel in nickel and nickel-bas(~d alloys, 7ney dcraonstrate tho huterogeneity of the self-
diffusion process and the significance of grain I)otindaries, temperarure and compogiiion or
structural' factors for the procosses of self-and ncwro-diffusion. Prismatic samples of
technically puro Ni, Ni plus 0. 01% B, Ni plus 0. Wio %V and of alloy lQi2ON80T3 were annealed
at high temperatures (I hr. at 1100C, 12 hrs. at 1100C, 9 lars. at 1200C and 2 hrs. at 1200C,
CRrd 1/2

ACCFSSION Nil: AT40,1640,;
respoctively; all cooled in the furnac(~ I.o ')00C, Lhon in free air), thon poli~,hcd CleCLI-olytically
63
and (~Icctroplated with Ni (Coat thickness u1) to Plated sampies were horriogi~niz(,.-I in
a vacuum, furnance at 700, 600, 1000 or 1200C. Lffvcts of structurai factors ~)n difljsion
'( . Ix
rate were stud.,,ed on cast or Jorged samples ol alloy ZhS3 which were f, ,- 7 S.
at I I -33C, then homogenized in argon at 80(j, S:io oi- '~50C. ILL wati lound thLL ,iolf-diilt.i~iion
-,f Ni proceeded mainly along the grain boundaril.!s within the rwige of ~JIA -1200C. S,-,:! -
U`iffij,ion coefficients ranged from 2.0 to 56.0- '(),2 cn,.~'Vsec f(,,r pulrt- Ni at, t-iO- and !2100C,
respectively and 0. 6 to Z8, 0 for alloy n2' `)I*,S0':':i at such temperawres. activation
energy was 24 800 kcal/g-atom. Coeffici ts of tLn I dius ion in ZhS3 ranged f rorn 0. 3 to
0 crn~/sec (for cast material) at en
113.0. 1 13 800 iznd 9,-i)C, respectively and from 0. 8 to 33. 0
for forged material. The ratio Qsurf/Qbull~ was 0. 75, 0. 62 and 0. 52, respectively, for ZhS3,
KH20N8OT3 and pure nickel. Orig. art. has: 5 tables and 7 figures.
ASSOCLATIOM. none
SUBMITT7,D: 09Dec63 DATE ACQ: 28May64 ENCL: 00
SUB CODE: MM NO REF SOV: 001 OTHEM 008
Card 2/2

41,
i,ate !-,~tlca-l

IcRr~-, -.. -I.
. I
" , -* --L .- 1 -1 - ,
. it of -,*,.e z - t:r - ` t~.e : '-- )'-r-) '.* c , i-. t Ical .'. - : ar~ ' u -
I.-,
'-~:ar. Te3h. FIz., 14, .:)s. I " 1);
li I , . '.

0
joe o o 0 (600990 0 00
0000*-0:00000000600000000 10000 W00*000000it
is to t, I
6 v a It a a -In It a an is v is 0 4 44 a 'to a 064
I Iit ofT
lo!"i , . - #I" C"fal 00
Af -00
i-00
oot
oes
008
:0 .0060
netweem aw StImIct'm I me sad&" at W&V= and 00
Stru'dum 41 grft ad RUNLAAR-) ;;0o
L P. AtIlres- Zhu r"4iDrVkr.Vh C=T 'd-! (journal
of Tchialcal Physics), V. IS. Mar. 1948. p. 3Q3-316- coo
0041
0 0
~00
WOOD
N t
It dog 00
U a I* IND f1k. a rw a 4 1 9 111 2
0a 0go 0 A ma Ill Ill of Cl it It of RO III fX4 at
'00 ~'000-0 -0-0 -00 4: 0000* 0 0000000**.Is 00 0 0* 0 0 * 0 0 0 *6see 0
0 0
- ------ -00 0-0 so 09~ 0 * 000 *-* a& 0 * 0"king00 ga * 0 * 0 000000

L.
C W
-I". r
I~onthl-,. Lif-~

7:: Vor o i:
T ITLE: eo ry o t h e 9 rx) c te r i s , i Cs "n P.,.c *.,-Orr . ',lc
Anpsrntus (-.eorlyn pnroqov.,:kh kh-r-kteris*ik fotowrifirtj.-,-us.n(--
go prilorn~
I. The ~~ole of the -pticni .7ystem ~f t~ie Annprs'us in the
Case of fndivilual r)! jPcts in t%e Vision Akea :-~ol' opti-
cheskoy sistpmy prilqrn v sluc~pye .)Hpl'nyk~ o~"ye~t-)v v
pole zrenly-')
FF
,RTn'TCAL: 7. urnnl nPuchnny i rrikl-ldn fo toiyrnf ii i ~ ino-, t )i7rnf ii
195,9, Vol ~, Nr 6, pp 443- '40
The author interprpt-~ th- theory of the threshc,11 cir-r-ctrr-
istics of p-. )t ;PrRphic apppr-tus nt the open sessions of the
'-ommission for _'cientif ic :_hotoprnp~y qnd of
the A.-) in 1 Pningr-il %;nd "oscow in recto` er an~ -'eceT-er
19r7. ';n this first PPrt ~,e is concernrA with t-.e contrast
in the re-l im-ge in the cnpe of in,:ividunl pre.,( oh.;ects lo-
cnted in f ields 1 ri,7hter or d-rker tl~pn the o! jeots t~~emspl ves
EquPtions for a ~eterminqtiin of the relevant t!iresh,-)ld cha-
racteristics are discussed. It is conclude,-' thqt, ,,p(-,n a
comiparison of the resulting finpl equations, it is possible
Card 1/2

The Theory of the Threrholl
T. The Role of the ')ntical
Objects in t~~r- Vision Area
SUEMITTE71:
'rarpc'ertF: tics zf tne np-r:~ *-s.
System of the AT)npritus in t"e of Tnlivi,1~1'91
to cover thresh.-)ld chpracteristics also in the cases o~ en-
tirely different objects, oplic9l systems an,! photograp-ic
anpAratus th;,t hA,ie scatterini~ properties.
There are 1. praphs, 1 dinaram and ' references, one of
is -soviet An;' 1 Pritish.
ecember 1,-,, 1017
Card 212

ITJ THOR Idoroz, L.P.
TI TL3 Formation of Images of Objacts , in a Field which in Brighter or
Daricer than the Objecti , by an Aberrationless Optical 3yrt(xG
(Izobratheniya bazabarratnionnoy optit,haskoy sistemoy otdollnykh
ob)ektov, nalchodyashchikhsp -4 polla. boleye i1i. meneyo svetlam, chc%m
stuni ob)olcty)
llh;RIODICA.L: Optica i Spektroskopiya, llj~181 Vol 5, Nr 6. pp 692-698 (USSR)
ABSTRACT: The object is a band in a field whi-h is either brighter or darker
than the object itself. -rhis object is imaged by an aberrationierF.
optical system with a circular &perturs. The author obtains an
equation which relates together the obie-A width, its contrast with
the surrounding field, thG c-ontrast between a point on tho object ax"5
and the surrounding field. the a parture of the optical system and the
wavelength used. xhis equation maces it possible to find the limiting
values of each of the listed quantities, when the other quant.Ltias are
-Ivan, as a function of the limit of sensitivity to contrast of the
recoiver used. The folloving special cases are considerod; contrast
in s. real image of a black band in a bright field as a function of th,3
object (band) width, contrast in a real image of a gray band in a fi,31d
Card 1/2 brighter than the band. contrast in a real image of a gray bqnd in a

,-)OV/ 19
Formation of' Dnages of Objects, in a Fiald which is Brighter or Jarcar tia-, V-.-n
0'ujoctG Tneinselves , b~ an -,oorrutionless Optical System
Viaid daricur than tqe -oand . rho f orni of the equition d eriv A by + Le
autnor dopo--ids -n whathar the objact is dar&er or brij;htar tho
field for a piven contrast of the object N7itti tho I,ioilll - : o .[-it, cd
vias usad to obtain this equation may be apolijd to 01 t", 46) f
other shapes, to optical systacus wkth othur oroporti~,s k-j 1")
whi ch have SCatt3ring properties. iho paper i,; anti.-(,)Ly ti,,-,orAt~:a]
Thero are 4 figures . I table and 2 rofaroacas , I of' wi-den i:3 .~ovi rt
and 1 :English -
SUBMITTED: November 5, 1957
C-ard 2/2

23(1)
SO V/77 -4 -1 /1,-,'
AUT. -OR; Moroz,
TITLE: The Theory of the Threshold Characteristics of a i,hoto-
graphic Instrument (Teoriya orogovykh kharakteristik
fotografiruyushchego pribor a~ 2. Problems Arising
During the Design and Operation of Photographic Instru-
ments (Zadachi, voznikayushchiye pri konstruirovanii i
ekspluatatsii fotografiruyushchikh priborov)
0
PERIODIC~*LL: Zhurnal nauchnoy i prikladnoy fotografii _J kinemato.,_;rafii,
1950, Vcl 4, Nr 2, pp 81-89 (U1,3SR)
A&3TRACT: At the open scientific sessions of the Komissiya po
nauchnoy fotografii i kinematografii All 3,313R (Committee
for Scientific Photography and Cinematography of the AS
U.~SR) in Leningrad and Mloscow in the winter of 1957, the
author stated that the threshold characteristics of a
pho-o-raphic instrument depend on the qualities of its
, Lj
optical system and its image receiver. If the optical
rv
,-lard 1/8

307177-41-2-11118
The Theor, of the Threshold Characteristics of a Fhotogra:~hic Instru-
ment, 2. Problems Arising During the Design and Operation of L-hoto-
graphic Instruments.
system is non-aberrational with a circular aperture
and the object is a strip of any given width, placed in
a field lighter or darker than itself, then due to
diffraction, the optical system will convert each emit-
tilng line into a band of energy dispersion. U~ing'the
grapho-analytical method of consideration f 1-/, the
author produced an equation connecting the following:
1) the width of the separate object in the form of a
stripi 2) the linear 8 or the angular Gc (in cases when
the strip is placed in a lighter and darker field than
itself); 3) its contrast K with the surrounding field;
4) the contrast KL between a point on its axis and the
surrounding field in the image, formed by a non-aber-
rational system with a circular aperture; 5) the apErture
of this system (the numerical aperture A or the diameter
Card 2/8

The TCeGr~ cAL' t-,~-ie, Thres':.ol~,' Charac-. _ristic~~ ~-_f ahic ln:~tru-
iroblems Arisinc- During the Def3i n anul e n t o -
ment
,-ra, hic instrumen.,.s.
D of tlie entry pupil); and S) the length of 'Q*;,ie wave
of the emission L, -
~k . If the object is darker than t-e
field the e-,uation looks as follows:
0. T,?4 JL8 (I - 0 /7D x -~- A At 0
and if the object is-liiiter than 'Uhe field;
0. egA~-4- A~
-Ki 1-k i
These equations -.ake it po.-,sible to find the nece_--.,=y,
particularly the threshold values of each of the enumera-
ted values when the remaining values are Jven. 1.3y con-
tras~ the relaLionship light-dark is understood in all
light
Card 5/8

The TI'Ieory of tiae Threshold Characteristics of a
ment Problems 1'~risinE ~)urin-- the Design and -:-~07'c'-
,-rapnlc :n-~rruments.
cases. The author defines sor,-ie of o,6her vu'---ies
more closely and demonstrates the accurac~~ of results
obtained by e-luations (1) and (1-1.) and other _iven
equations, and the :--r-a,)hi(, method of solution whica per-
mits --reater accuracy. He shows how to calcul-:'Ue by
integration (see table) the value of Kiot (imair
- _,e cc)n-
trast in the case of a b':.a,-.k object. in ',I~e field,
when K=I) and to present in the form of a
relationship between Kiot and the values "V""e -P
A-n sin u - the numerical aperture, of the sys' 'em (n
is the refrac,ive indlex of tllie medium in front. of the
system; u is the al:erture angle from the side t.~.e "11'e"i
of the objects). Ile derives equal"ions (" IJ
ai,(I W) !,vhich -.,re simplifications of (L) ay.d
(I"J. 1"he author then 't-irns to formula'ting an~,'
Uard 4/E.

SCV/77-4-2-1/18
-'he -.-eory of the Threshold Charact-eristics of a-! '- o-~oz-
I roblems Arising bring: t',,,-e __esio-n an _4 -.--era-. i __L O__
ment,
ln:3truments.
typical problems, ari3inE d~iring the _~esi~_7n ar.al use of
photo:-raphic instruments and instruments cons--'st-in:, of
an optical system and an image receiver. 1"nese are as
follows; 1) Finding the size of an object of a I-liven
contrast with the field, formed by an optical system
_L
W4 th a previously given con rast on the receiver;
2) Finding the least contrast value between the ob-
ject and the field at which the instrument will dis-
cover its existence there; 3) Finding the necessary
value of tl-~e threshold of perceivinG the contrast of
the instrument's receiver so thLt tIe la ter may dis-
cover the existeLce of an object of a -iven size and
-4 111 t
concrast t 11,
._" -e f-*Leld; 4) Finding he necessary value
of the apeTture of an optical system from the side of the
image area ~in pa_-Licuiar, the value of the focal diStar~ce
Car 5/8

SOV/77-4-c_ -111 --1
The Theory of the Threshold Characteristics of a Photographic Instru-
ment, 2. 1 roblems Arising During the Desigr- and 'U'peration of ':,hoto-
C T
F, r a nhi Lnstruments.
of the instrument's optical system) at which a -iven ob-
ject of a Given contrast with the field will be at the
iimit of instrament dscriminaticni 5) Finding 'he
necessary value of the numerical aperture of an optical
system (or the diameter of it1c- entry pupil) w`- ere an o Ib-
ject of given contrast wit'n tt.,e field will be repres-
ented on the receiver with a previou-sly given contrast,
-S) Finding the necessary value of 'he numerical. apert-
LLre of an optical system (or t"ne diameter of its entl-ry
pupil), where the instrument will still discover a
given object of a ;-iven contrast with the field;
0 C,
Finding +-he --reatest distance to a given object of
a driven contrast wilh the fie1d where the inStf,iment will
still discover its exi5tence; various other problems.
The author finally draws t1ie following conclusions 1) Equa-
Card 6/8

,-)'OV/77--)4 -2-1 /JP-
The -1 .~eory of the Tlareshold Characteris tics of a
ment 2. Iroblems Arising During the Design and Cperation of
I C)
~Sraphi - Tnstruments.
tions have been derived which canec, ',~-Ie wide',-. of a
separate obiject in the form of a strip (,w',,en it is
placed in a field lighter or darker thin itself,'., its
contrast with the surroundinC, field, the contrast between
a point on its axis and the surrounding field in trie image,
f,-,rmed by a non-abern-itional optical system with a cir-
cul:~r apk,rture, the aper,L-,ire of this system 1-ind the lenjIth
of the waves of emission 2) Phe form of the equttion
differs according to whether the object is ligLter or
darker than the field, at a given contrast between the
object and the field. A connection between both cases
has been established. 3) The equation makes it ;)ossible
to find the re-uisite or threshold values of any of tU',.e
enumerated values, shen tne remaining values a2e
in connection with the values of tf':e t'--reshold of contrast;
Card 7/8

SGV/77-4-2-_'/1;__-
The Tl~eory -~f t,,.e Thresi~old Characteri sties of a ithoto'-,,raphic Inst ru-
ment , p. i rob] ems AT~iS: nj_r During the Desi (.-,n and Oper,% t1ion '-)f
phic 'n.;Lru-ments.
perception of the insti.,ument receiver, 4) ")ome 16ypical
problems of threshold characteristics, arising during
the design and use of pho*.o.:~-r-aphic instruments, ~-.-,ve
'11 1 ;'al "Inal -iven
been formulated i.' solved. ysis It -is been ,
of these solutions. There are I table and 5 ~3(.~vie~ re-
rerences.
1.
71, 195'7 and Dece:Lber _11, _95'17
i't.! 1 -2: _~ D Jecember l.. , 1957
~-rd 8/8

MOROZP L.P.
Theory of the threshold characteristics of the photographic mechanism.
Part 4: Reproduction of details in the form of separate slits of
any width and any contrast with the field by the complex function
of the optical system and photographic layer. Zhur.nauch.i prikl.
fot. i kin. 6 no.2;13G-138 Mr-Ap IO'l. (MIIRA 14*4)
(Photographic optics) (Photographic emulsions)

Howlis-L-171-1-
Imaging of separate linear objects
with the field surrounding them by
a gramila layer. Opt. i spektr. 10
(optics)
of different width and contrast
combining an optical Qatem and
no.2:2/+9-256 P 161.
(HIEUt 14:2)

4308
S/o5i/62/013/005/014/017
E032/E3i4
AUTHORS: Kirily4k, Z.O. and Moroz, L.P.
TITLE: The effect of stray light on the diffraction pattern
of isolated line objects
PERIODICAL- Optika i spektroskopiya, v. 13, no. 5, 1962,
734 - 739
TEXT: Stray light due to sources inside or outside an optical
instrument is superimposed on the image produced by the latter and
may have an appreciable effect on the threshold characteristics
of the instrument. The formulae derived in this paper
may be used to take into account the effect of the background,
whatever its origin, on the contrast of the diffraction imagesof
line objects (wires or slits) and their immediate neighbourhood
for different object widths, wavelengths, aperture of the systems,
Contra.,;t between the object and its immediate neighbourhood and
contrast between this neighbourhood and the general illumination
field. Using the approximate energy-distribution in the
diffraction pattern of a luminous line, derived in earlier papers
(L.P. Moroz, Zh.nauchn. i priki. fotogr. i kinematogr., 5, 81,1959;
Card 1/2

S/051/62/o.13/005/014/017
The efCect of .... E032/E3i4
Opt, i spektr. , 10, 249, 1961 explicit expressions are obtained
for the threshold widths of darl, objects for different contrasts.
These expressions have been verified experimentally by the micro-
photometry of diffraction patterns due to wires 0.02 - o.1 mm
in diameter with differently illuminated backgrounds. The results
obtained are summarized in a numerical table which indicates good
agreement between experimental results and the theoretical formulae.
These formulae may therefore be used in practice to determine any
of the quantities list'ed above when all the others are given.
There are 2 figures and I table.
3 UBM ITr ED: October 4, 1961
Card 2/2

MORCYA, L.P.; AYUKWOV, A.Kh.
Possibility of detamining the effective deptih of the yield of
secondary electrons in the ion-eleatron emission from dielectrics.
Tzw. AN SSSR. Ser.fiv. 26 no.11&1322-1327 N 162.
(MIRA 15:12)
(Secondary electron emission) (Dielectrics)

-J; 4v
v ......
Xh;`
lox
tta (in", t ti ~1~
v
Vane, tC.at
a y-, i~,
up .1963"
-vror. re. tudL#4~~'- --~-h6gativ
e
ra
idiia- bile:
no
trow:'Oompo
Ilants w
tilthd ave .4:~ tll~fga, ~Cbmnj
id mb4,L*%kftdTLt
n rom 4GV"~'f bad, 4 -.dt~ --Tit "un, or:a
z or. I.S
AM.,~.The char
'd gilt oh~',df, th~
-OP(
Iiidlik"10ith nat of
-a: thick-
all~ iu-~'
t-0

7 7
Id
3 0 02 0
to
Me 10
&V th-
ou,4mlssloti P-hiddd",'qu2'te!"d ff even V, i
C-Itheid 3-`~wjt a Ats& a0
and,.in-
Ls-
a _0
emrgy.---:an acrea 2.n ma's
n4 d d
zMar us- t b it," Ut
Th the, ra io;: a
p9 e a of
ry~ qp. ow;
no 'i 6d drd' z4~46'
a
-anergy-
can-, -ftc
TM
UBIIM.

MOROZ, L.P.; AYUKIMN07, A.Kh.
Use of the secondary ion-electron emission method in the
comparative study of the depth of penetration of various
inns into d'electric films. Izv. AN SSSR. Ser. fiz. 2-8
nn.8:1395-1400 Ag 164 (MR-A 17:F)

MCROZ, L.S.
"Musamwit
Sensory innervation of the cranial mesenteric artery Irwith summary
in Inglishl. Biul.eksp.biol. i med. 43 no.3:107-110 Mr '57.
(MLHA 10:7)
1. 1z kEkfadry naormallnoy anatomil (zav. - prof. G.F.Ivanov [deceased])
I Moskovskogo meditsinskogo Instituts. Predstavlona akademikom A.D.
Speranskim.
(ARTIRUS. HESICYBRIC, Innerv.
sensory Innerv. of cranial mesenteric artery (Rua))

Vc, WS; 000600015L 00
A 1 0 J ?
1
I AA 0 LL it it
$
.

Tko tatio d dfiluittoci (a omitutatlito d Fe M C- '00
4 Wins, And L. 14. MOM. Stal I.N. a. 1. 1, No it, A7 4"
itol 1); 4, C. . 1. IS. M471 Two kindt,d diffu4m sm '00
f~` sent: a "rmetive" and a "puie"

11311rd ot the pre
-00
0: Iit t c Itirturf a chein cituthinatento k fnmcd om the %tat -
f&.V if the crine"I"I Inalefial while in the tallf'r the -00
00. lifftio'big toram'Sisrati, thigh thr.Ty.l. utl%i,,d
-
"
9 0
00 difictiarnoti"uph-
Reactive
thicemen(tdmitteriaJ. .
&A by the forniatkiti cof carbides when Fe t, rmeni,l *0
with C The Impimt coor is the cementation A .-F~
1111110,
00 1'hm ptm.to 6 umore cognpiciL when a steel alloyed with
larbide4fortniets elcuient. 1* crinend"I T,, su-iy Ott. -00
pfom4 steel spetintem wm 4std. in a varying degree -it fi
-00
W ur Xfo; then thew tpecimem wrrr cemented in a ms%t
Tbers-%ulivatilmitfoubl, -00
ementotsm we detailed and illustrated with phmiiiisri-
'90
Kraphs \1 11-h
-09

tie

Ito; -00
+
I

lo 0 0
e 0 r!0 0 0 0 0 0 0 0 0 41, 0 0 0
s
000 do* 0000 00 *OGG 0 Goo*@* 0.0 as** 0 0 40 0 0 00 0 0 4

OM t oil t of, lot? 0. . "R
A
COq
Mochaalaul (d illauglug of fratlevo Iota atif )a Itan, ivad
wChel M 1. 4 And L. .11 MUtill, ) I e, k /'* ,
A (I !% " It A It, :0-3 WGMM, Cylts"Ific
imit .11.1 1
1
/I
"vI,1" 'lip 60 air I, 11100ed Ill M." W. N# 414.1
I
;
11-011 "1
ill it, '01 lit- Alict -4mg. I' 'A Ill" I Ilsill flilsh -11,v-
air lurt-I I(I Ain't -1.1"f(A 1'. 'Ifelf, , tillAr"Crapill, Awl
0
ID e -,,v I1.1- . C., A....."I I I I lit(
It, I., *(I,, 'tulvt
0 mi t- h, C', uml
se '1111-9.11
"HI-11 It .-Ild -IIA, All MI, 0% A it) FC; aftl,f 1.1tact
!.', l"'. At P-Ill U . ht,l. at UNK), Air
Ow ljvvt at% itil,rim-fall" , I"Atmi.
.10, I-W h, lay" . Jid -In All Mo fWl
,I" 4illI' l4w
dw .4w of 'I'di'lljil IV
I -m.t %I,, I've W, vIIIII'llill. If
I( lit,- itil,mi,vAili, utuln] , in 1. y,.r,
0 I'll MIA' flit ~falll- If thv condition, of flic
"c"14,"isiplo if-mv , dwwiwicl~. At a dirtmitc ilwwkn-.
flivic I, a uddirti droiA A thc Mo (W, -utl,tril. ilrbsch It-
_'Ati- If th,r dwanoll till t'llip aull, le
C11:1- .,tb ojAt:r,&,mjj tlarkilic,, f2- DifTu,i,,n of Si
..F,,
it, I-, ~WA min At II.W. wild ~olu. II St ot
bar. at 11213". br.t -layrr voltnpd. Fr,lw 14-,, So, -cInd-
Ivt,t X.S.Z" St (3, tic in pl,. If) b-, at IOXX)' I'M 3
hr, At 1401", tint Isycir Frile,, ilct-und-lailve, orntAl
with _ItAI -In of It, ill -I-c % Ill. W, 11"t of Bir
A S 6 - I L A IIIIALLUARCOCAL UYEAVATUIRE CLASSMoCATICh
0-
I -v#
?1 01, 1: 1; A I A,
I is Po U's b f All
. ..,
J." A I
'. ..... . .
It, It I A
11 I_fIJ,InJE N,
v N It N
-4f "I , -hd -I.. It I., % I 1., 4 _4 I
fkl.,t .
Wir'l "alil"i %011, -III'l .-1t-1 till
Ill hill,
41 Ill At lit V. I AIN. _Iltl
1 41 A, mi,
-
11 All \A I lit of !I:,.
411.1 -own --ur, Ill I .... 1,-r of
It,, A, I,:j"
. A ..... of kill
tf;
In
-N, 'till n gl-, I- tf,_" (h, to
Alf 1-19111"1 M.W_ -,,all hr. at im;* a
at -fid -11i of it,- Ff"'A' It" forccolifir
T-U11%, 'AulAO&IMAIM I,v nittAlogrApily. Aml %_
t4v it 1, IllitfTed that thr lir,,t Italic Alf ~)Ijj
-o Iy
.*,If a. 1)), 1*14, 111 dwit;
"war.,iltv. flip tat, "I -bl Ill ill, IfIlArtn"J411t,
-111P1 in Ow pur,- uut,il. th, fIrri- -,,, I.
InIv 41-1,tit 1h.
-fifli, ill,- Ltt,-r
fil"lon Jv Al"?`-- -,Ih laroir-,m, I,f:
Thv
'101 . ...... dal,d it
lh~ "Pur".
phir, j,jju,j_I --Mpf It' M
n. A 2
--,;, hal A llwh~,
W. NI. 11, nd I Il,n
DID
Os"
T
u 0 11T 1W 0 so I it-
111 Oflit Sit mi mi 11111typ
OIDID1601
:00 00 0:00 0 0 0 410 0 0 Ole eeie so e* 0 6 e 'Do:
01,61,
*so 00004
90
.0o
of
Zoo
0
--so
tie 9

M14
.jjeChAW= Of WS DtMWOD LD thC CdfU.-3t4!;O3 of
clewwal
J3,
111-iyuw th . ......... 1.0-. '4
.11l.'rlnwfjtA imem
Arbil, j-&r lt~
flu. "Mroting jx'wdrr
Im-Lal '%ilmi.r rrr V.
R-Lit., h". ri'~ I. f-M.-
C (3 hm. i. tint I~P-r V:ft
tf-f
"oh
mf .. ..... q- ....... m the
ti.- 1-- v,,rY Aaf~r-,nt da~,Lo,n
-1 tltn&ryl AIIIN Ol \',Sl. -1 W.
pi.". in the 'f-' 1vt ... it- in
Itt.-A 'd ffm V-11ttrIt, fit, 10.1 1
--I WrIA-al ot r1i.
1-P -.-,it .1, [h.
"n~' thr"'),ch h' t
4., w-t lu& tfi-~ -xi,r in if,,- -t
fl lljl'~Sl ;".I
''I %.
10 3-

A
LAL
sit 7`411?ITT Ittlittll Mitt
Iv
rVvIft
I 1 11
A
: A L-1 a
0 A
--- - --- - - --
--

IF
M
sichiectilem ad thele eff a fleets annedict, On Mi, saris.
ett
*
1hrrct drtn
of the 4 0'. 1"""
hy -V .4
-00
ctft$dctecI. I..S.m
va. 'r J(
SS_R.j
Ia. 171-M)OWA) On ~4111111_ 111 3 cillfreent i-asijunt .
.
'teswItumeatt"i ox x .4 X 4 ,, 4 'treA.-4
, -00

ste~6,14
X 14 X que-b-i is, 14)1, N'a()It A. * (.w 1-4 let.. ft.." -1 12. 11 _~' -i'l " ~ "
hunn" It, at W41
.
'
I
l
00
AF
at 4-M'. rinved-I .the firuiell hard,w" A lit, Intel.. at 4 Cdown it, 0.(1(13
le anle /
in
;. gise. t
.
lowl of 3WWW) he.) Pits"ref agaill.1 The CAjFt..J returns le.trizisollatum to 0- C .4 't-1. t.-J.-I -4
*
; 00
81' (0 12 t. 11 49";) sti linciu, juerva- ot 14 with I'; C at 1trainty III It A. .4 fl-vtlois M '.s.
coul-I. That the 1 'Go
an~ cilevil annil-Alluell trull, I I'litulirl or.1filit till" ju~ hold. derms 4. Itur lowest C -W-t 1, ."1
"
v
t

0 41' ObtAluril fur VAIIIIIIIII. ft. 11tilelli,le iff.Mil aral.111 2 lit. , FulureafrIl 6.1 *-' lit, At 0.". 1-41,
I
SICTI .41111
ic
." -00

llf
Fullerelfills at 4110. 4.141, two), 117,11% re'l. . Jilt 4). 12' r C. 'utu. ever. it - a 41.3.1411. 4 115, 445u-, , r-p . it r
~j
0 - 3.1%3.7. 4 1. 4.5 nine., re,1, . (,it 41 tx,,~ C
if . ,"I trullerfed anal ItiorlitAIMI. It - .5 it I lif- ITAIAHO b-in
.
13.15. 3.4. 31145, 4.2 tsun.. rellp. Sititwr it was shown by (it the R-CeC 1111CIS IMWCS that tile ITIMIAIIIIIII 14 tile
J x-ray investigation, that thr C "Intent ot tile 0-phase orl , effe*t 4 C coriteert on the hard--d- ,.,I sAll ..111 1.
I
atencidniq of a ceino. fabove 44111".dor, nil( de
ful on the ,v th, do,I.-mly
,I cither wunK the h2rdnm~ i4 neu &W
al I-, C of the orel. the ficilear i reIs,r (W with I;C
r
i. (fur to the cArbide phaw~ Tile VAnati,-ii cit JR A% a fit, lljghrr~ i~f~t,vtr .4 the -.1.1 1.- IF, I-

function of "; C "insists in a c"urv III the res"tesuev 1. ~Irrl~ than the d74" liver. wher,- they a-
deforenaticen c4 the m grains as an effect 4 t1w eunu I-It lear.11O.
ValFiatinsil cit the hardll- .4 feel .I
a cutside. Extral"4416M of the If.', C hisee, Ili Jr. C
( . .
, NIVCH ( CePtIvent, in frrtilt lit dIIr rill IF, IV 1-0 A' hittlar
giveii the heirdus- 4 it,, pls,tw. thr rre.W .96 the pcol~ll- .4 Ili, '. .41.1 111. 11 , t Ian...
illvr,l~l I I the &-vurription .4 a .4 tile "ou'll, if it,, 4 ... All- .4 11 .. ...... 41 ... a 1, 1 01-1 -00
111 'Farbute at onctly `;L' - 0 twtior, .4 [till-- mesuill"'u", lietren 4.5 iudn. sawl I(Ou hr, . At .h 1. Irr,A,.F,tc,f 00
it the C&IIIISIC I)ILLW 111~111-JWArril At 11 mescaline only shifts the line listralld to steed t4, lower
at III-, C. the hairchl- .4 .. at velp-) --1.1 be, -60
3.52 seem. 4% again%l I viA trine to o,; C . .00
J 00

&16 it& 4#TALLUVOK.i WFORATI-11 CILWOPKATOGO I,
4
4
7 4'*

U 5 If .4[) is L S is lid 0 4 1 ill W
it 2 11 a III It

00 the
hirb,.-f-urimi
00
of
00
so
00
so
GOP
00
of
Os
00
00
9e:
0
040
00
Ifvp fin Arust-Wifig A,
.-t At" Ow nature .f the
"I-fored .1111t mu'l g;.... 1.
11, th.- ~1'4" 'll.gram 14. 1. '' .I It
'he B-';C ploone t. det.l. "ely by tit,
the 14-1 -ti-I scolely by a ~Iusnjte 4 1-q-t.- .j h,
ph&w I'VIdirntly, the (tioun. of thr cart,,.1,* jmf1j,I_
&ft&ln% R celtiCod value m annealing al,ivr 4jo, . .1"
P"Mty ~" lottiv Ite a Jet$[ (art,w .11 t. .....
IW10,q4tilit' If jjjd%t he "Mj-Ijjj!e,I that Ill.- tf_jjjj,,%
.-f -i.pirted 41 311,11 4#111'
It-unted, tout .,oatflnurs ago 1067.11,
of
00
66
00
00
09
00
00
odi
66
00
00
00
00
00
00
400
00
0
0 0 e 0 0 0 0
0 0 0 0 0 0 0 0 o o 0 0 0 0 0 0 0 9 0 0 0 Sit 0 0 0 0 0 q a 0 0 0 0 0 0 0

0 0 0 o 4`6 -40 0 o 00 *so
sojes,00909*090040060 00000000000060;;&
AA CkLI tjl~ I Loot! 140
00 A~
00
So
*0
-00
oo
00 %fair of .4ran Its Annealed Harien.14c. ;I,, i
00 L. 8 %Ifgp and Yu S. T.-riifl.axov Zhu,""? l"'46 -00
-0161 4'-;' 1.1ki (3--kIrnut ,f Ttwhnivnl Phy-w-1, fee
00 19. Mar. 1919. p. 3143-390.
oo The slinve wax lnw%tijratv4 by X.ray diffrviefim,
go usiv)g swimpris of carlwn Meel water
f',,m goo,r. and annealed for fifferent -00
aynd at Mertnt temoeraturex. Afetlind f .-%jvri.
so mental inv"fluation 1% dexcritied. fIxta nrp ,bnrt,,.f :j: 40
00 and ts~ulated 12 ref-
00
~2 t
-100
'awf7"
-,2z
too
It .....
o'
it K La n
0 es 0 sees 0 0 0 0 0 00 00 0
0 0 00 0 0 111 0 0 0 000 0000 9 0 0 0io see* 0 0,110041110 -0 --0--0 0 --a 0-0 0,

PHASE I TREASURE ISLAND BIBLIOGRAPHICAL REPORT AID 35~ - I
BOOK Call No.: TN672.V8
Author: MOROZ, L. S.
Full Title: STRENGTHENING OF ALLOYED IRON IN THE PHASE TRANSFORKATION
Transliterated Title: Uprochneniye legirovannogo zheleza pri fazovom
prevrashchenil
Publishing Data
Originating Agency: All-Union Scientific Engineering and Technical
Society of' Machine Builders. Urals Branch
Publishing House: 3tate Scientific and Technical Fublishin House
of Machine Building Literature ("Mashgiz
Date: 1950 No. pp.: 11 No. of copies: 3,000
Text Data
This is an article from the book: VSESOYUZNOYE NAUCHNOYE INZHENERNO-
TEKHNICHESKOYE OBSHCHESTVO MASHINOSTROITELEY. URAL'SKOYE OTDELENM,
THERMAL TREATMENT OF METALS - Symposium of Conference (Termicheskaya
obrabotka metallov, materialy konferents1i) (p.225-235), see AIr 223-11
Coverage: Substantial increase of hardness of practi6ally carbonless
alloyed iron at tempering Is discussed. The experimental
results indicate that the hardening of,-,:~-Iron crystals oc-
curs because of deformation at vr)l-ume change in the process
of phase transformation of-?(Fe-)-_---(Fe.. The appearance of re-
81dual strease:a in the cryutal iattice and the breaking up
1/2

Uprochneniye legirovannogo zheleza pri. fazovom AID 3513
prevrashchenii
of' the grains create the strengthening of alloyed Iron which
is the substance of "phase hardening".
Comparison of physico-mechanical properties obtained by the
phase and mechanical hardening leads to the important con-
clusion that the 3trengthening of alloyed Iron at plastic
deformation and heat treatment Is subjected to the same laws
of mechanics of materials. However, the mechanical state of
crystal lattice at "phase hardening" has a special nature.
10 charts, 2 tables.
Purpose: For scientific workers
Facilities: None
No. of Russian and Slavic References: 5 Russian (1941-49)
Available: Library of Congress
2/2

Y,O'tczt L. -).
Me tal lof-re -)hy
Causcs fcr th~ ~1 'f I *us ior: o!' In tr-rferer.c, ';I nz :-, -n X-re-.- ! - ~ -ar-!,:rjf!e4 (*h,":.Cn-
free alloys of iron. Zhur. tekh. riz. -,? nr,. -1, 1992
9. Nionthly L~ist r,.1 Russian Accessi~-,ns, Librrary ()f' C,,rigr-ss, A ug~-Us t - '~q -ix, 2U, I r I.

MORO7. 11 0.
USSR~hy;ics Alloys, Plasticity
Card 1/1
Author Moroz, L. S.
FD 364
Title Significance of plasticity characteristics, reflecting certain sides
of the physical state of alloys
Periodical Zhur. tekh. fiz. 24, 425-432, Mar 1954
Abstract Experimentally establishes expediency of considering separately
uniformly-distributed and concentrated deformations of alloys under
tension and discusses significance of each kind of deformation in
investigation of various factors which have effect on physical con-
ditions of alloys. Studies deformations of carbon steel and its
characteristics, such as yfeld point, tensile strength and reducticn
in area, versus chemical composition, structure and heat treatment.
Fifteen references, all USSR; most 1948-1952. Graphs.
Institution
Submitted September 18, 1953

141GIRTZ, t L . 3 .
bTSR/MRtals Hardening
Card 1/1 Pub. 153 - L2/ i
Author Moroz, L. S.
The phenomenon of internal cold hardening during the pclymorphi- '~on-
version cf ga-mma-Fe to alpha-Fe
Per.ludical Zhur. tekh. fiz. 24, 705-7!4, Apr 1954
Abstract :Triestigates the influence of volumetric variations, during the pc~_'Y_
merphir conversion cf gamma-iron to alpha-iron, upon the internal
structure and mpchanical propertieE of alloys. Attempts to ~,onne,t
the tcughening caused by cold hardening of the alpha-iron crystals.
fe'lLewing the --hanges in volume during the conversion of gamm -Fc- tc
alpha-Fe, with the changes in the mosaic structure of the al,-OYF,
Inotitutioa
Submitted September L8, 1953

ALITGAU23S. 0.S.. kandidat fiziko-matematicheskikh nauk; BONSHTSTN, M.L..
kaad.idat tekhnichookikh nauk; BIAMPMR. H.Te., doictor tekhaicheakikh
naak; BOKSHTITH, S.Z.. doktor takhnichaskikh nauk; FOLKHOVITINOVA,
Ts.N.. kandidat tekhnicheakitch nauk; BOR7.DTKA. A.M., doktor tekhni-
chaskikh nauk; BUNIN, K.P., doktor takhnicheskikh uauk; TINOGRAD,
M.L. kandidat tekhnicheskikh nauk; VOLOVIK. B.Ye., doktor tekhniche-
alcilch nauk Cdeaeaasdl; GAHOV. K.1., inzhener; GNLLIR, Tu.A.. doktor
tokhnicheakikh nauk; GORAILK. S.5.. kandidat tekhnicheakikh nauk;
GOLIDEOERG. A.A., kandidat tekhnicheakikh nauk; GOTLIB. L.I.. kandi-
dat tekhnichaskitch nauk; GRIGOROVICH, V.K., kandidat tekhnir-heskikh
nauk; GULTAYZV. B.B.. doktor tokhnicheakikh nauk; DOVGALICVSKIY. U.N.
Irandidat takhnichaskilch nauk; DUDOVTS.SV, P.A., Icandidat tekhnichs-
skikh nauk; KIDIN, I.N.. doktor tekhnicheakikh nauk; KIPNIS. S.Kh.l
inzhener; KORITSKIY. V.G.. Icandiclat takhnicheskikh nauk; TLANDA, A.F..
dolctor takhnichaskilch nauk; LEYKIN. I.H.. k-andidat tokhnichaskikh
nauk; LIVSHITS, L.S., kandidat takhnicheskikh nauk; LIVOV, N.A..
Imadidat tekhnicheakikh nauk; KALTSHEV,K.A.. Irandidat tokhnicheakikh
nauk, HWMSON. G.A.. doktor tekhnichaskikh nauk; MINKXVICH, A.N.,
kandidat tekhnichaskikh naulc; L.S.. doktor tokhaic-heslcikh
nauk; MATANSON, A.K.. Imndidat4%aT'lL-,-U'9kikh nauk; MAKHIMOV. A.M.,
inzhener; HAKHIMOV, D.M., kandidat tokhnichaskikh nauk; POGODIH-
ALUSAM, G.I., dcktor takhnichaskikh nauk, POPOVA, N.M., kandidat
talchnichaskikh nauk; POPOV, A.A.. kandidat takhnicheakikh nauk;
RAKHSHTADT. A.G., kandidattokchnichaskilEh nauk; ROGELIBARG. 1.L..
kandidat takhnicheakikh nautc;
(Continued on next card)

ALITGAUZICN, O.N.---- (continued) Ca rd 2,
SADOVZKIT, V.D.. doktor tekhnicheskikh nauk; SALTTKOV, S.A..
inzhenar; SOBOL9Y, N.D., kandidat tekhnicheskikh nauk; SOIDDIKHIN.
A.G., kandidat tekhnichosicikh nauk. UKANSKIY, Ya.S., kandidat
takhnicheakikh nauk; UTEVSKIY, L.M.. kandidat tekhnichaskikh nauk;
FRID14AN, Y&J.. doktor tbKhnichaskikh nauk-, KHIMYSHIN. 10.F..
kandidat takhnicheskikh nauk; KBRUSHCHEV, K.K.. doktor tekhniche-
skikh nauk; CHARNASHKIN, V.G.. kandidat tekhnicheek1kh nauk; SHAPIRO.
M.M., inzheaer; SHKOLINIK, L.M.. kandidat takhnicheskikh nauk;
SHRAYBER, D.S.. kandidat tekhaichaskikh nauk; SHCHAPOV. N.P.. doktor
takhnichaskikh nauk; GUDTSOV , N.T.. akademik, redaktor; GORODIN. A.M.
redaktor izdatellstva; VAYUSHTiCYN, Ye.3., tekhnicheskly redAktor
[Physical metallurgy and the heat treatment of steel and iron; a
reference book] Netallovedenie i termicheskaia obrabotka stali i
chuguna; spravochnik. Pod red. N.T.Dudtsova. N.L.Bernahteins, A.G.
Rakhahtadta. Koskva. GoB. nauchno-telchn. izd-vo lit-ry oo chernoi
tsvetnol metallurgit. 1956. 12o4 p. (MLPA 9-9)
1. Chlen -korrespondent Akademil nauk USSR (for Bunin)
(Steel--Heat treatment) (Iron---Heat treatme,t)
(Physical metallurgy)

. - ~L~.Ctt, IAKHTIN, Tu.M.. redaktor; VADDV, N.A.. redaktor
JUN". - 9~0
izdatelletva'; IVUSOS, I.M., takhnichaskiv redBktor
LIFIne structure and the strength of steel] Tonimia struktura i
prochnoott stall. Koskva. Goa. nauchno-tokhn. izd-vo lit-ry
po charnoi i tevetnot metallurgit. 1957. 158 p. WaA lo:6)
(Steel-Notallography)

7
Translation from Refer~t;,-::v% z,, Nit- v USSR,
AUTHORS Moroz L S Kr,sin Yi; D T F
T rr LE T he St I'l-0 i, of I' I f -t 11: 1111 1 llo-0 1, 1 in,
PER1OD,CAL V SI) Most c)\.k- AN SSSP 172-
193
ABSTRACT An I l)VCS' 1011 ~-k dS M (I(. of I lit (.ff(.k I (.)I 1o%,. I cnl!)" Irc t.
!crIgtK of load nu I me tl()t( !!I n" nd wl,e, f~( to"s oil tlif,
I T r d ~ a
modulus Of Of I)CILLS1-11 s me I t ed - n ii t. e i ( - - t v ( u
furna( c Ti t- duthors dis ( ov v - c d -1 S ;~- I d I ff(' t- 1!( :5 t* 11 bT 1 t %t 0
notci-mg SN. in ii-wt~!s of s t, a t t, s ri i v't , i 16! 5 wlr_ %k s (I t, i
the :-alio bctAct~ii ti-e sp,c f~t dt~fo-rri~t oti wo-~ of ~rilp.~t slrolcll,:;!_~
of smooth spec meris -And I~c ~k of notched Mesnage., -1 vpe s:) i m c n s
Ti which 1-.s . high SN is ~Iso scfisiflvc Io Ihe st~,tv of I!.,- e lit.
notched spe( inivits ni,,x tnurii onivio (it
with whi( 1, Ti i-cf,lins i tolv-,ible SN b 111 t I . - s f : g L i t i i v v I
ing upon 0 -ind N ( ontent Ti,v -Wens-tv of the offccl of It oil hw i,,,
determined by the size nd typ(- of' T,fI prec 1PIT11tiOrl ki:IL h dcp(-nds
Card I /Z upon the ( ooling rrjlc fr oni 11 c lemprr -iliji-c of , -100"C' sf,~ ( 1,

The Strength of TitaniurTj
7
bending tests of notched spec imons showe(l thtl the MagnIlLIdt' Of Tilt' b( AIIIILI~ deflec-
tion and the deformation work Lip to the appearan(-t~ of thc first ( r t(k - jis wt-11 as
the work of propagation of the (-ra(k thi-ougl- tI'v t.lltlr(~ se( tioll of !, t. _";wk :mt.:I it
room temperatUre, art, less in Ti it-;iti Ili SKi-L--i !it (kil'inlit tc.itilig _171
with 0 0007% 11 oxhib,ts no (old-brittit-tiess what(,%erl 5LIT 'xl~on Ilic( tod !)" In-IpW"-
ties, in )arti(-iI1ar by H. it be(omes c~old-briiilt- An int rt,as,, i*i 11 t on'"!~l lu
0.0 1-, decreast-s ., b v 7 ~:, "0 ai 9 6 o CT,,,, t,ti,ors d%aii~ t.- to
ex,)Iain the plivsical naturo of of Ti bv TI-t, lock S,j of fo~~'O-ublv
oriented hvdride incluslonb It was disco, t-ed i!'-it he st r-i:n rate 1~ j~, i.o vffe( I
on the ductility of smootl-, bpet iniens of '17; vn-( ht-d \k ti, It
Gard

t. t, ,,, ~, -Z It. % .
AUTH(YRS- Moroz, L. S. Dr. Tech. 5r.., Nemchinskiy, A. L., Cand, Tech. Sc.
_Pa__aER_ov_, Dr. Tech. Sc. , Pro,". , Shurakov, S. 3. ,
Tech. 3c.; and Bendryahev, 0. L., Cand. Tech. Sc., Hev of the
Central Factory Laboratory (Tsentrallnaya zavodskaya 1;,boratoriya)
TITLE: Brittle Breakdown of Steel and Steel Parts (Khrupkiye razru-
sheniya stali i stalInykh detaley)
PERIODICAL: Zavodskaya Laboratoriya, 1957, Vol. 23, No, 1, pp. 123-1;5
(U.S,S~R.)
ABSTRACT: The first fair of the above authors present a review of Lhe
book, "Brittle Breakdown of Steel and Steel Parts" by Ya.
M. Potak, which contain3 389 pages and is published by
OBORONGIZ, dated 1955. These critics find that the aLthor
used much material based on his own investigations, IT*y
state that the book fills a need in the metallurgical in-
dustry and contains little that. merits crit3cism, The
author listed last above, Bendryshev, mak-s a separat( re-
view and finds that the book will acquain*. wide circles of
Card 1/2

TO
!g V
a
IV.
'01
~ 41
'Ork-

v45
I- P.
fln q0
19 SIR D
21.
31
a A 41 a
H 'N F JJA
a, i9i re 4
Sol
A& SAVAd a
A a

MOROZ, L.S I
- - _,4 doktor tekhn.nauk; MIGIN, T.E,, inzh.
Machaniam of the hydrogen embrittlement of steel. Fetallo-
vedenie 3:51-57 159. WIRA 14:3)
(Steel~liydrogen content)

MOROZI L.S., doktor tekhn.nauk; KHESIN, Yu.D., inzh.
Study of the mechanism of hydroger. embritt2em-ent of titanim
and its alloys. Metallovedenie 3:74-87 t59. (MIF! 14:3)
(Titanium-Hydrogen content)

MOROZ, Lq,_�-j doktor tekhn.nauk; XIMIV, Yu.D. , Inzh.
Anomalous metal grain growth in vacuum. Metal2avedenie 3:32-2-
313 '59. 14:3)
(Vacuum meteilurgy)
(Metal crystals--Growth)

al qmcm JO W4~m uvwv ~r~ov a -i;i_7q-vz6 rm-V -1 -Mw
991 ~n - .-T3
7.
in T-7-1 J. ~~.Q -0 .4 -rmQ
PSI ft"..z 'I _TTW
q,
'P2
PlT" -T%jjd--V ,Wtti -TTW nn!.f ; -?C-M
-11-Ty "I P_ -1-1-MU J. Aunl ... u -1 .4
I~r .1 "~O
r- Td ... W.Tx T_T.Q-kl J. npTr-0 '.., .,,=.Z
T-,ns P_
J. Almq~s
Z.TT~_Tpw J.
tW ...... qN T-T-.pAl J. qWTV-V
vi I.M .11 P- -1~1,1 j.
'-3 P"
P_ q?TR 1. ..ScUTUrm J. _jVM LKLI ..m
T-T~W.N .1 vw
'A P_ ;. ~.PTP-z -a -A
N -9 '-.In J. 1-ir -7 --.
J.-C In %.-.TjiTq.S ..9-prd, * 71;.Mm
'S 'I r'- T-T-q-1 J- IM-4 ~.
61 I-V J- --mjw
T
1- 6.1 .6 -H s M~ J. ZwTrm
J.-ts 9-U-TTY J- 1--JJX --n V- R-T11-9 PM-M
T -Ing J. ~.N .-.Jw T-TM.%L J. -%.m -V
.P-74.- - 0.71TT~.d
'Eq ..T.Tsft u
-74-T-- P- (C V_
TA,-Iwd Twluwzrzm Alatn cn mviw fv sLoTTv jo mlm~ P" -w-4-mns
'Y,m'-iT- (~ (-TT-Av-- 1-n-4- '-Ti-woq- '-n-P-t) 7~~T J- ~Twr-
..r- .~-ftn -1,~ IV ~ITW WTT4T4q 01 -X~VM WTunqM V~
r- J. -n - --,Ov -01~
j: W.u". q% (I j. M IZNUI=
P--A"
1-.d . 72.-j- -AJ P-V-ft-I -1 3- -MZ--nm -M :lPDAM
I-ps -woz rtm A-Irl fo~wm r-7.4--m JO ".PTVM .WAd" -1 .0
*P"""d ..Td~ 00?-C d O~c *"61 .T9-dpm -7 I(C -.0
'--T-TWN J. T-T.&W) C -9 'An.49 TF-0qq ffttrv".rT"A"

'YffP-7F I B00Y EXM ITTATION SOV/4575
Moroz, Lev Solomonovich'. Doctor of Technical Sciences, Professor; 13-c-ris Borisovich
'tTe-Mi~tVrn'Y 11yevich Polin, Leonid Vladimirovich Butalov, Saveliy
I
Moiseyevich Shu-11kinY and Aleksandr Petrovich Goryachev
Titan I yego splavy, tom 1: Tekhnicheski chistyy titan (Titanium and Its Alloys,
Vol. 1: Commercially Pure Titanium) Leningrady Sudpromgiz, 1960. 515 P.
Errata slip inserted, 4,200 copies printed.
Ed, (Title page): L.S. Moroz; Ed. (Inside book); Z.V. Vlasova; Tech. Ed.: N.V.
Erastova.
PURPOSE: This book is intended for scientific workers, plant engineers, and
students in advanced courses in schools of higher technical education and
tekhnikums. It may also be used as a manual for designers and industrial
engineers (with the exception of mechanical engineers).
COVERAGE: The book presents data on the structure, phase transformation, and
physicochemical and processing properties of commercially pure titanium.
CarT116-

Titanium and Its Alloys (Cont.)
SOV/4573
Shape-casting, vacuum metallurgy, plastic deformation, welding, and soldering
and brazing processes for titanium are d-iscussed. Special attention is given
to problems of constructional strength and to titanium reduction processes.
L.S. Mo z wrote section 1 of Chapter 1, Chapter 2, and sections 1, 4, and 6
0T_=R7Mrr 3. B.B. Chechulin wrote sections 2-6 of Chapter 1, sections 2,
and 5 of Chapter 3, and Chapters 4 and 9. I.V. Polin wrote Chapter 5;
L.V. Butalov, Chapter 6; S.M. Shullkin, Chapter 7; and A.P. Goryachev,
Chapter 8. The authors thank A.V. Smirnav for his advice, and I.A. Bytenskiy
for assistance in editing the manuscript. References accompany each chapter.
TABLE OF CONTENTS:
Foreword
Ch.-.,I. Physical Properties 5
Atomic and crystalline structure 5
- 0 tic 1 properties 12
Eplectaronic properties 15
\Electrical properties 16
5: !'T et~c properties 21
6. T evqZtl properties 23
Bibliograpo 33
car-T-2716-

Titanium and It- Alloys (-'ont.)
SOV/4573
Ch. 2.- Effect of Principal Impurities on the Structure and
Phase Composition of Titanium 37
1. Regularity patterns of a general nature 37
2. Effect of 0 2~ NV cy 112 ~ Fe)and Si impurities on the
structure and phase composition of titanium 42
Bibliography 56
C11. 3. Mechanical Properties 58
1. Mechanical properties of chemically pure titanium.
Effect of impurities. Commercially pure titanium 56
2-Heabst7deal properties of commerciaUy pm*t~ titanium 63
-3.-SkIr-tioix-properties 80
Characteristic features of titanium constructional strength 91
4~-,Kffeet-ef-cold working on mechanical properties and structure
of titanium 125
Effect of heat treatment on mechanical properties and
structure of titanium 134
WbUography 144
Gar"AL

6~692
s/l8o/6o/ooo/oi/olV02?
E193/El-35
ALITHORS: Moroz, L.81,--and Khesin, Yu. . (Leningrad)
TITLE: ~fri~estigation of the Mechanism of Hydrogen Embrittlement
of TitaniumAand its Alloys
PERIODICAL: Izvestiya Akademii nauk SSSR,Otdeleniye tekhnichesklkh
nauk, Metallurgiya J. toplivo, 1960,Nr 1,pp 111-1.22 (USSR)
ABSTRACT: The object of the present investigation was to study the
effect of hydrogen on the mechanical properties of a.-Ti
and titanium alloys of the 0 and a+3 type (the
constitution diagram of the Ti-H system is reproduced in
Fig 1; wt-%, top scale, at-%, bottom scale)., The
experimental materials comprised: technical purity Ti
(U.T.S. 2 55 kg/mme_ at room temperature); a two-phase,
Ti-base alloy containing 2% Mn, 1.3% Fe, 0.8% Ci,
1.42% Mo and 1.2% V; a two-phase, Ti-ba3e alloy
containing 5% Al~ 3% Mo and 3% V; and a 0-alloy,
containing 15% Mo~ After hot working, all these alloys
were finely-crystalline with the average grain size of
0.04 to 0.07 mm, after a vacuum treatment (15 h at 7000C)
Card their hydrogen content was less than 0,003%. Two methods
i /16 were used to introduce hydrogen into the test pieces that
were to be employed in the subsequent tests: the

f"'02
S/180/60/000/01/016/027
K193/EJ35
Investigation of the Mechanism of Hydrogen Embrittlemerit,-.,'
Titanium and its Alloys
electrolytic and high-temperature diffusion method,
The electrolytic treatment was carried out in a 0.1 N
H2SOL~ solution, containing 20 mg As203/litre, at a ourrent
density of 0.2 amp/cm2, After 2 h treatment, the
concentration of hydrogen in the specimen varied from
about 0.2 wt-% in the surface layer to 0.1% at a distance
of 0.1 mm from the surface, and 0.01% at a distance of
0.2 mm from the SUTface. The high-temperature diffusion
treatment was carried out at 700 OC, hydrogen being
obtained by decomposition of titanium hydride; after the
diffusion treatment the test piece was heated and, to
avoid the effects of ageing, the mechanical tests were
conducted within 24 h. To determine the effect of heat
treatment on the constitution of the alloy, the effect of
the quenching temperature on the structure of the a.+0
alloys was investigated with the aid of X-ray diffraction
Card technique. The results are reproduced in Table 1
2/ 16 showing: quenching temperature, OC; proportion ~%) of
the p-phase in alloy Nr 1 and Nr 2 (for composition see

66 6 9 2
s/18o/6o/ooo/o!/016/027
Z193/E135
Investigation of the Mechanism of Hydrogen Embrittlement of
Titanium and its Alloys
the heading of the table). The effect of hydrogen on the
mechanical properties of the technical purity titanium,
annealed at 650 OC7 is illustrated by data given In
Table 2 under the following headings~, H2 content, wt-%;
as (yield point, kg/mm2) ; 'qf (reduction of area, %);
ak (impact strength, kg/mm2). It will be seen that
whereas neither the yield point nor ductility (as indicated
by Nf) of the specimens were affected by increasing
hydrogen concentration, the impact strength, determined on
notched bars.. failed catastrophically, This effect is a
direct consequence of the nature of the Ti-H constitution
diagram (Fig 1), Solubility of H In mw-Ti varies from
0.18 at 300 OC to O~002 wt.-% at 100 OC; after slow cooling
from temperatures above 300 OC, hydrogen is present in
titanium in the form of fully preoipitated titanium h7dride
platelets (see the photomicrograph, Fig 2); when titanium,
containing less than 0.18 wt-% H2, is heated to 300 Ocy
Card hydrIdes dissociate completely and a solid solution of H
3/ 16 In Ti is formed. On quenching from this or a higher
temperature, a super--saturat9d, precipitation-harderiable,

Dob~2
S/180/60/000/ol/ol-,/027
E193/E135
Investigation of the Mechanism of Hydrogen &brittlemeriz;
Titanium and its Alloys
solid solution will be obtained, Thus, a titanium
specimen with OX3% H, quenched from 500 OC, had an
impact strength of 7 kgm/cm2i after ageing at 200 OC its
Impact strength decreased to 1 kgm/cm2. Similar results
could be obtained by prolonged room temperature ageing;
this is illustrated by data, given in Table 3, which
shows values of ak of the H-bearing Ti specimen after
quenching from 500 OC, and after 1, 10 and 100 days'
ageing at room temperature. Electron-microscope study of
the ageing process confirmed the hypothesis tftat, in this
case, embrittlement during ageing is associated with the
precipitation and coalescence of titanium hydrides; this
is illustrated clearly by the photomicrographs (X 2_350)
reproduced in Fig 3 (a - the m1crostructure of an
H-bearing, Ti specimen in the quenched conditlong b - the
same microsection after 7 days' ageing at room
Card temperature) which show the increased proportion of the
V16 hydrides as well as the grain-boundary broadening In the
aged material. Regarding the mechanism of the embrittling 11K

68692
S/180/60/000/01/016/02,7
E193/E135
Investigation of the Mechanism of Hydrogen Embrittiement of
Titanium and its Alloys
effect of hydrides, the authors base their con3iderations
on the experimental data reproduced in Tables 4 and 5.
The effect of the rate of deformation on ductility of
annealed, H-bearing, a-Ti is illustrated in Table 4,
which showss H2 content, wt-%; elongation (6, %) and
reduction of area (N4f %) for specimens tested ~t the
rates of strain of: M 2 mm/win, and ~II) 2,10 mm/min.
The effect of the test temperature on the ductility of
the same material is illustrated in Table ~, showing:
H2 content, wt-%, 6, and 4f determined at +20 20 and
-60 OC; (the specimen with 0.03% H tested at --40-0c
failed in a brittle manner), It can be inferTed from data
given in Tables 2, 4 and 5 that brittleness due to hydrogen
is not revealed by standard tensile testsq conducted on
cylindrical specimens, and only becomes evident in the
presence of a notch, at high rates of strain, or at low
temperatures. These J'acts can be interpreted In one way
Card only; titanium hydrides, while possessing some ductility,
5/~16 have low resistance to rupture, if the normal. tensile
stress in titanium is lower than tkie rupture ,trength of

s/18o/Wooo/oi/016/027
E193/E135
Investigation of the Mechanism of Hydrogen Emby1ttleme,il,
Titanium and its A.1loys
the hydrides, the effect of hydrogen will not become
apparent; if the normal stress is raised above that
critical value (by introduction of a notch, increasing
the strain rate, or lowering the temperature), cracks
are formed in the hydrides which reduce the 3trength of
the metal to a level depending an the propoylion of
hydride platelets present and on their size, since these
factors determine the number and dimensions of the
cracks, This is illustrated by data reproduced in Fig 4,
where the true tensile strength (SK, kg/mm2) of H-bearing
titanium at --196 OC Is plotted against the quantity and
dimensions of the precipitated hydrides, points a,6
and 0 relating to: (a) specimen quenched from 500 OC
(low hydride concentration); (6) specimen quenched and
aged for 2 h at 100 OC (medium (,-oncent-ration of hydrides
of small size); 63) specimen annealed at 1+00 OC (high
Card concentration of coarse hydride particles), The
6A6 propagation of crar;ks in hydrogen-embrittled titanium is
assisted by the internal tensile stresses. prasent at the

66692
s/18o/Wooo/o L/ o 16/02 7
E193/E135
Investigation of the Me(,hanism of Hydrogen Embrittlement of
Titanium and its Alloys
edges of the hydride platelets owing to their higher
(in comparison with Ti) specific volume. Oxygen,
nitrogen, and carbon additions increase the sensitivity
of titaniiun to hydrogen embrittlement, since they promote
propagation of cracks; tne effect of aluminium. is
beneficial since this metal increases solubility of
hydrogen in titanium. The effect of hydrogen on the
mechanical properties of a 0-type, 15% Mo-Ti alloy was
studied next, The results are reproduced in Table 6,
showing-, condition of the alloy (degassed; hydrogen-
im regnated by electrolytic. treatment - 3 h at 0.2 amp/
cm~)i U.T.S. (cr]3, kg/mm2); yield point (aS~ kg/mm");
6. %; 1,~ 9 %. It will be seen that none of the
investigated properties were affec..ted by the presence of
hydrogen. The results of experiments on specAmens with
higher content of hydrogen (introduced by high-
temperature diffusion), quenched from 7550 OC ', are given
Card in Fig 5, where -~-r of specimens tested at the rates of
~1/ 16 strain of 2 and 2-00 mm/min (crcsses and circles..
respectively) Is pLotted against the hy(irogen c.,ntent

'~ _- c '7~ -
S/180/60/000/0 1 /0-7 ,b/02
E193/E135
Investigation of the Mechanism of Hydrogen Embrittlemei.,~
Titanium and its Alloys
It will be seen that as long as hydrogen is in the
solution, it does not affect the ductility of the
0--phase; precipitation of hydrides in the 0-pha3G
causes the metal to fail in a brittle manner, this
effect being attributed to notch-sensitivity of the
p-phase. The hydrogen embrittlement of the cL+O alloys
is next discussed, Two alloys of this type, containing
20 and 50% of the ~-phase, were investigated. Their
mechanical properties OS, 6, and w), are given in
Table 7, the figures in the fIrst and second sub-columns
for each property relating to the hydrogen-free specimens
and to specimens subjected to 24 h electrolytic
hydrogenization treatment. It will be seen that,
whereas the yield point was not affected by the presence
of hydrogen, the ductility of the alloy (6, W ) decreased
sharply. It was observed, also5 that fracture of the
Card hydrogen-bearing specimens started at the surface, the
8/16 first cracks appearing already in the elastic
deformation range (see Fig 6), The effect of the

68692
S/180/60/000/01/016/027
E193/E135
Investigation of the Mechanics of Hydrogen Embrittlement of
Titanium and its Uloys
variation of the content of hydrogen, introdu^,ed by
high-temperature diffusion, is Jllustrated by data given
in Table 8 under the following headings; H2 oontent,
wt--%; W., % of the alloy containing -DO and 501 of the
P
0-phase, specimen of the alloy,. containing 20% of
the p-phase and 0,1% H2, failed in the brittle manner).
These TeSU1tS showed that the embrittling effect of
hydrogen was more pronounced in the alloy with a lower
content of' the 0-phase. The effect of the deformation
rate is Illustrated In Figs ~ and 8. In Fig ?a, ,.4f is
plotted against the rate of strain (V, mm/min) fOT an
alloy containing 20% of the 0-phase, curves 1 and 2
relating to specimens before and after the electrolytic
hydrogenization treatment, respectively; the corre3poxn-
ding curves for the alloy containing 50% of the ,3-pnase
are plotted in Fig -b, Tn Fig 8a, I& is plotted aga-1 st
L Ln
Cai-d V for the alloy containing 50% of the ~--phase, curves 1,
? and relating to spe(Jmens with 0,025), 0,0SO and 0,119
9/1.6
of hydTcgen (Int T' -D d U C ed by tigh A.empisrai,~ire ~11,LfAisl0r,

S/180/60/000/01/016/027
E193/X135
Investigation of the Mechanics of Hydrogen Embrittlement of
Titanium and its Alloys
treatment) respectively; the corresponding curves
(I and 3) for the alloy containing 20% of the ~-phase
are plotted In Fig 8b. In this case, too, the
proportion of the O-phase determined the behaviour of
the alloys. The ductility of specimens containing
hydrogen, introduced electrolytically, increased with
increasing V, approaching the ductility of hydrogen-
free material at V = 200 mm/min, this restoration of
ductility with increasing V being less pronounced in
the alloy with 50% of the 0-phase. In the case of
specimens containing hydrogen introduced by the high-
temperature diffusion treatment, the restoration of
ductility with increasing V was slow in specimens
containing 50% of the 0-phase, and did not occur at all
in specimens containing 20% of the O-phase and 0.1% H2,
The effect of the constitution on the sensitivity of the
Card cL+P alloys to hydrogen embrittlement was revealed also
10/16 by the results of impact strength tests, conducted on
notched, cylindrical specimens 8 mm diameter (depth of

68o9a
s/18o/6o/ooo/01/016/027
9193/E135
Investigation of the Mechanics of Hydrogen Embrittlement of
Titaniim and its Alloys
the notch 1 mm, root radius 0.55 mm). The results of
these tests are given in Table 9, showing: H2 content,
wt-%; ak, kgm/c~n2, of specimens containing 20 and 50%
of the O-phase, However, it is pointed out that tensile
test at slow rates of strain is a more sensitive method
of revealing the hydrogen embrittlement of titaniwa
alloys of the a+p type. The difference in the
behaviour of material containing hydrogen, introduced by
different techniques, is attributed to the fact that
hydrogen introduced electrolytically (i.e. at room
temperature) can dissolve in the O-phase only. This was
checked by X-ray diffraction analysis, carried out on a
complex, Mn-bearing alloy, whose alloying elements,
however, did not affect the solubility of hydrogen, The
results are given in Table 10 under the following
headingst constitution of the allu (relative
Card proportion of the a,- and 5-phase ; lattice parameters
1.1/ 16 of the a- and 0--phases in the degassed alloy; lattice
parameters of the cL-- and 0-phases in the alloy with