SCIENTIFIC ABSTRACT KISHKIN, S.T. - KISHKIN, S.T.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R000722820008-2
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: September 18, 2001
• Sequence Number: 8
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

69386
E073/E535
Influence of PolyMOrphou .sTransformations on Diffusion in Titanium
high strength of the interatomic bonds. The following
conclusions are arrived at: the
1) The coefficient of diffusion in a-titanium at
transformation temperature is larger by about two orders
of magnitude and-even more and the activation energy of
the process is half that of p-titanium. A qualitatively
equal relationAs observed in commercially pure titanium
but the diffusion mobility in this is considerably lower
and the activation energy is higher than in iodide
titaniumi.~
2) The difference in the diffusion parameters of M and
P-titanium may bedue to differing strength of the
interat.omic-bonds.-or-may be associated with structural
features of:a-titanium.
3) Struc.tuval changes In titanium in the process of,
diffusion annealing lead to an acceleration of the.process
of diffusion.
There iii:~ 3 figures, 2 tables and 17 references, 7 of
Card 4/4 which are.Soviet and 10 English.

83238
S/129/60/000/009/001/009
ILI 10 2109 E 19 3/E4 8 3
AUTHORSt -Kishkin. SeT.o-Member-Corresp6ndent AS USSR and
Polyak, B.V"~_Candidate of Technical Science
TITLE: Kinetics of Rupture of Heat-Resistant Alloys in Cree~o
PERIODICAL: Metallovedeniye i termicheskaya obrabotka metallov,
196o, No.9t pp.2-6 + 2 plates
TEXT: To elucidate the mechanism~of rupture of Ni- and Cr-base
alloys under prolonged load'at high temperatures, creep tests were
conducted in vacuum (10-5 mm Hg) on flat test pieces with one of
the sides carefully.po.lished.,so that the changes in the micro-
structure could be periodically observed with the aid of a low
power (x 200) microscope, without interrupting the tests. To
supplement these studies, an electron microscope was used to
examine the fine microstructure of the test pieces on the
completion of the tests. The following conclusions were reacheds
1) During the first 30 to 50% of the life of specimens, tested in
creep, microcracks' are formed at the grain boundaries which are
normal to the direction of the.applied stress. With increasing
duration of.creep, the number and the size of microcracks increase,
leading ultimately to fracture of the specimen.
Card 1/2

83238
S/129/60/000/009/001/009
9193/2483
Kineties,of Rupture of Heat-Re,sistant Alloysin Creep
2) Th~jalloys tudied in the course of the present investigation
fil (exhibited relatively high elongation (10 to 15%Y
(ZhS3 91
7~
wii-ensu"j cted to short-time high-temperature tests but failed.by
brittle fracture when tested in creep at the same temperaturev
the elongation under these conditions being only 1 to 3%. This
difference Is attributed to the fact that in the former case,
fracture is preceded by plastic deformation within the grain%y
whereas in the latter easel fracture is brought about mainly
the formation of cracks at the grain boundaries, little
evidence of deformation within the grains having been observed.
3) In the case of the ZhS3 alloy, in the as-east condition, the
formation of cracks takes place later than in the material that
has been subjected to pr6liminary mechanical treatment. This
effect is attributed to thefact that the growth of cracks in
the cast alloy is arrested by the carbide precipitates.
4) The formation of microcracks can be delayed and the life of the
specimen inereased,if a thin surface layer is removed from the
surface of the specimen by electrolytic polishing. There are
8 figures and 9 references& 8 Soviet and 1 English.
Card 2/2

_. doktor tekhn.nauk; ILTM, A.A., kand.tekhn.nauk;
KIK01=09 Y.Y., kand,takha,nauk
Characteristice.*of metal failure at high temperatures. Trudy
MAI no. 123:5-46, 060. ~ (MIRA 13.-B)
(Beat-resistant alloys) (Therval. stresses)

KISEKINI S.T., doktor tekhn.nauk; KLYPIN, A.A., kand.tekhn.nauk;
KARYAKINA, N.V., kand.tekhn.nauk, NIKOIMMO, V-V-; CHONOV, M.N.
Investigating the relation of structure and properties of
mateirials for gas-turbine blades to the duration of their use.
Trudy MAI no.123:25-34 160* (MIRA 13:8)
(Gas turbines-Blades)

BOKSHTSYN, S.Z., doktOr tekhn.nauk; GUDKOVA9 T-I-9 kand.tekhn.nauk;
ZHUXMVITSKIT, A.A., doktor khim.nauk, KIsHKIN, S. T., doktor
tdc hno nauk
Effect of prestressing and of the creep process on diffusion
inside and along the grain boundarieso Trudy YAI no-123:35-40
16o. (NM 13:8)
(Crystal lattices) (Creep of metals)

KISEK19 I- S.T., doktor takhn.nauk; BMWIMVA, G-F-, Inxh.
Strength of alloys In contact with sodium* Trudy KAI no.1230-45-
52 160* (KIRA 13:8)
(Alloys-Testing) (Sodium) (Nuclear reactors-Vaterials)

KISBXIN, S.T., doktor tekhn.nauk; SINICWTNOVA. V.P., kand-tekhn.nauk;
O.Y.. inzh
Failure of nickel-bass alloys under the effect of repeated,
loading. Trudy KkI no.123t6g-75 060. (KIRA 13:8)
. (Nickel alloys-Testing)

85379
r3o S10321601026101
B016/BO54
AUTHORS: Bokshteyn, S. Z., Gubareva, M. A., Kishkin, S. T., and
TITLE: Study of the Process of irok4ecrystallizatton by the Method
Lror
of Radioactive Isotopes
PERIODICAL: Zavodskaya laboratoriya, 196o, Vol. 26, No. 10, pp. 1111-1114
TEXT:~ The authors studied the behavior of atoms at the grain boundaries
during the recrystallization of iron (content in %: 0.021,C, 0-014T,
0.011 S, 0.67 Si, 0.07 Al 0.08 Mn, 0.06 Ni, 0.033 CU). Samples of this
iron were covered~with Fe;9,. in anaealing, Fe59 spread due to diffusion
at the boiindaries between the metal grains. This permitted an observation,
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 out into samples (10y, 1Ox 20 mm). The riveted
layer (70-809) was removed by electropolishing in perchloric and glacial
acetic acids. An Fe59 layer 1.0 IL thick was electrolytically applied to
Card 113

85379
Stud.y of the Process of,Iron S)1032/60/026/010/007/035
Recrystallization by the Method of Bo16/BO54
Radioactive,Isotopes
the polished surface. Subsequently, the samples were deformed by
compression by 10-16% (Fig. 4) and by 45-706 (Fig; 2). Figs. 1-6 show the
autoradiogram (a) on the left,'and the microstruc ure (b) on the right
.on microphotographs. During exposure the samples were protected by a film
1 V thick 0% of Zapon varnish in the aolvent PAB (RDV)). To produce the
autoradiograms, the samples were exposed for several days on photographic
plates or films HOVOV4 (NIKFI)t type tjP(MR). The autoradiograms were:
compared.with the microstructure,pictures which had been taken by a
microscope of the type MWN -8, (MIM-8). Next, the recrystallization
annealing was carried out (Figs, 3v 5-6). A Table on p. 1113 gives the.-
hardness and the methods of treatment for some samples. On the basis of
their methods, the authors succeeded.in observing the behavior of grain.,
boundaries during plastic deformation and subsequent recrystallization.,
It was proved that,iron recrystallization at relatively low (15%) and high
(50-70%) degrees of deformation causes no essential change in the position
of atome.laying at the boundary of deformed grains. With a considerable
structural change of the metal after a double recrystallization, as well as
Card 2/3

85379
Study of the Process of Iron S/032/60/026/010/007//035
Recrystallization by the Method of B016/BO54
Radioactive Isotopes
after polymorphous w-*1 transformation, the atoms at the boundarfes of
the initial bodies are not:displaced. In contrast with recrystallization$
plastic deformation is accompanied by a considerable displacement of atoms.
The results prove that the displacement of grain boundaries during
recrystallization and the subsequent growth of grains is connected with a Y
specific mechanism which differs from the ordinary diffusion~mechanism.
There are 8 figures, 1table, and 15 references: 4 Soviet, 1 US,.1 Dutch,
1 French, and 4 German.
Card 3/3

34547
8/659/61/007/000/036/044
D205/D303
AUTHORS: Kishkin, S-Tot and Polyak, E.V.
TITLE: Kinetics of the break of heat resisting alloys inthe
creeping process
SOURCE: Akademiya naukMSR. Institut metallurgii. Issledolrn_
niya po zharoprochnym splavam, v. 7, 1961p 295 - 3J8-
TEXT: The heat resisting alloys used at high temperatures and stm-
see are disrupted mainly along the grain boundaries at very low pla-
stic deformations and the whole process is considered to be slow.
Microcracks are first formed which then develop until a break oCCurE6
This work is concerned with the kinetics of the break of industrial,
heat resisting Ni-Cr alloys taking into account external factors
(temperaturep timep stress) and internal factors (structurep state
of grain boundaries and of,the surface layer). The vacuum metallo-
graphy method of investigation was applied which permits direct ob-
servation at high temperatures and stresses. Microphotographs taken
at various time intervals describe the kinetics of break between
Card 1/3

S/659/61/007/000/036/044
Kinetics of the break Of heat ... D205/D303
2
700 900'd for stresses~of-up to 60 kg/mm . Development of the
breaking pro cess is discussed* After 30 - 50 % of the life time of
the sample microcracks'app *par.on the grain boundaries, directed nor-
mally to the tension stresseso In.time the number and dimensions Of
the cracks grow, I causIing the~material to break. Increased stress
accelerates the process which~proceeds in two stages; Gradual de-
velopment of the cracks on'the grain boundaries followed by a fast
final break. No appreci Iable internal slip was observed in the grains
of the Ni-Cr alloys.at high temperatures and at usual working stres-
8es. The break occurs by the.development of the cracks at 1 3 %
elongationg while at very high stresses (of the yield point order)
the elongation reaches .10 - 15 % which is caused by very intensive
internal slip. The surface'damage on prolonged heatingp connected
with the oxidation and burning out of some of the alloying elements9
accelerates the development of the.cracks, lowering the durability
of the material. Surface protection ist therefor~q required to en-
sure longer working life. The coarse structural non-uniformity
showing itself on the surface in liquation strips and oxide films
causes premature crack developments and break. Removal of the dama-
Card 2/3

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job 10/002/011
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poiiti6h of thd test 1i '64stilitiAd stif 46a !aye ris of
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4,116YO hoatta taking
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or thik pir
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inve sti gated i .-Alloy0a 'pt ~thc-tyVd M4)T:,(31437)- atter 6 hr
and obali i1i
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in Gi oxides and carbides Are, 600&01~r 1140i layar I takes
plaas by means of 0"05 9/01C 'imll 6;N ii (Otiii i and 44 w 66`1~ttfx,
CIA

27832
3/032J61/02-7/010/002/022'
Phase analysis of surface layers of B110/B101
elements)
E1617,
is not dissolved Lit
and only selectively
poor in-alloying
at E1437. - When operating with 18t the boundary between layers II and III
may be-determined owing to-the.appeara .nce of the o(I-phase in the anode
deposit. Layer II of E1617 is dissolved-in 81 under continuous control of
.U solubility in 18. For this purpose, the analytically" weighed ~ sample is
immersed �n 18 and, unless it diseolves here, it-is dissolved for~10 min,
in 81, the deposit.is removed, dried, weighed, and the cycle is repeated
up to dissolution and separation of the W -phase "in 18. Layer, III
consisting of solid solution (poor in alloying elements) and ckl-phase on
the basis of Ni (Al,Ti), as well as layer'IV of initial alloying composi-
3
tion, are dissolved in 18. The anode deposit 'separated in 18 and 81
(layqr.,IIj E1617)-is filtered off, and washed out with 0.0 electrolyte
24.
solution up to negative Ni reaction. Electrolyte and rinsing water are
,unit 6d-,'evaporated, filled up to 200-250 ml;-50 ml of it is mixed with 10
1ILl A2 504(1.84) and heated. H202 is added to the dark-brown liquid
obtained. It is heated up to destruction of H 202' filled up to 100 mlo
and the elements are determined. Anode deposit I is molten with KHSO the
40
Card 3/5

S/78
013 51/0Z7/010/002/022
Phase analysis of surface layers.of..#, V107B101
melt is dissolved in 5~ H 2 SO 4.7 and filled up to 200-250 ml. According. to
X-ray structural and chemical analyses, layer I '(UP to 0-005 mm depth) is-,
str ongly enriched with Cr, Al, and Ti. It consists of Me 203 (Cr203, Al 20V
NiO,TiO 2) with trigonal crystal,,stiuoture, the parameters of which are -
similar to those of Cr 0 In layer II (in-0.027 mm depth of EI 437 and
2 30
in-0-40 mm. depth of E1617), as in layer I, oLl- and carbide phases are
destroyed through Cr-, Al-, Ti and'C diffusion to the periphery, and t1he
oxides are formed. Layer III is ~0.10 mm depth in E1437 and,-0.15 mm in
E1617. In E1437~ the Me 0 are enriched with Cr in peripheral layers, and
2 3
with Al in deeper ones, In E1617, Al 0 already e"xists at small deptht
2 3
which suggests a missing equilibrium state. Gas :turbine blades of 3N437A
(E1437A) operating at ~TOOOC, where uniform dissolution was difficulty were
tested in this way. Layer I was missing (mechanical wear). Impoverishment'
in chronium was found down to 0-075 mm. The Ti content of the surf 'e
layer was constant. The Al enrichment at a certain depth cannot be
explained. Destruction processes on the surface starting at the grain
Card 4/5

27832
0/032/61/027/010/002/022
Phase analysis of surface layers of B116/Biol
boundaries are explained by deep oxygen,.diffusion along the grain
boundaries. N. M. Audneva, N. A. Shumilina, X. V.- Smirnova, and A. N.
Sokolov~assisted in the experiments. There are 3 figures, 2 tables, and
4 references: 3 Soviet and-1 non-Soviet.
Card 5/5

-33464
-Jly~ 11-i !t kA% S/129/62/000/001/007/011
E073/E333~
AUTHORS: Corresponding Member of'the AS.USSR,
Lozinskiy, M.G., Doctor of Technical Sci6nces,
Bokihteyn, S.Z., Doctor of Technical'Sciefices Professcw,
Sokolkov, Ye.N., Candidate of Technical-Sciences-
TITLE: Influence of high-temperature plastic deformation
on the'mechanical properties of heat-resistant
nickel-base alloys
PERIODICAL: Metallovedeniyel termicheakaya obrabotka metallov,
no.l,.,1962, 38-40 + 1 Plate
TEXT,: Two Ni-Cr-base alloys were investigated: the low-carbon
3OH437ra (E-I437B) AlloY of the a 'tandard composition and' the
.3"617 (E1617)-alloy, containing 0.12% C and additions of W and
Mo. The alloy E1437B was subjected to the following'thermo-
mechanical treatment: blanks of 16 mm diameter were first zoaked'
for 8 hours-at.1080*C and'rolled,at this temperature at &.rolling
speed of 4.5 m/min to 30% reduction. 0.2 to 0.3 sec after
deformation, the blanks were quenched to supercool the austenitw
Cardl- 1A

33464
5/129/62/000/001/007/011
Influence of E073/E335
and to retain the structure, produced as a result of high-
temperature plastic- -deformation. The blanks were then
aged at 700*C for 16 hours. Blanks of.the alloy E1617 were
heated to 1~00.*C and stamped in a press, so that an average
reduction of 30% was achieved; this was followed by---quenching-
in watero The-blanks were then agedat 800*C for 16 hours.
The results-of static tensile and-impact tests-at room
temperature ate given in Table L. Studies of the influence of
thermomechan1cal treatment on the creep strength of austenitic~
steels revealed that recrystallizatlon should be prevented
during high-temperature plastic deformation since it would
cancel out the beneficial effects of the thermomechanical
treatment. Mi6rostructural investigations correlated .
with the resulti of mechanical tests.indicate that the increasein
strength and'ductility occurs even if recrystallizAtion has not
been fully suppressed. The increase in strength is
attributed to.an increase in the quantity of the
carbide phase, to changes in the finely crystalline
Card'2/4

33464
S/129/62/000/001/007/011
Influence of E073/Z335
structure of,the material and to texturing. -The largo increase
in the ductility of-the-investigated alioys is obviously due
to the abAen6e:-1 of intercrystalline fr~acture.- The following
participated in the experiments: N.I. Korneyev; T.A.Gordeyeva,
Ye.I. Razuvayev, O*N. Podvoyskayat M.N. KozlovAj
L.M. Strizhevskaya, T.A. Volodina, N.F. Lashko, E.V. Polyak,
G.N. Korableva, A.V. Bulanov, M.I. Spektor and I.G.-Sk-ugarev.
There are 2,tables:and 7 references: 4 Soviet-bloc references
and 3 non-Soviet-bloc The three English-language references
mentioned are: Ref. i: ~E.B. Kula, J.M. Ohosi - "TASM", v&52,
1960; Ref. 5: DJ.Schmatz, J.C. Shyne, V.F. Zackay - Metal
Progress, V-76, noi.3, 1959; Ref. 7: E.Bi Kula, S.L. Lopata
Trans. AIME, v.215i 1959-
Card 3/4

33464
S/129/62/000/001/007/011
InfluOnee of .... E073/E335
Table 1:
Mechanical Properties
Alloy -Treatment Vb*29 4r. 5, a HD
b kf
kg/PW2 9/mM2 2 df
k % kgm/cm own
EI437B Standard (reference
specimens) 97.0 25s0 2049
TMO 119 3240 30-7
Standard (reference
E1617 specimens) 71-7 103-7 14.6 io.1 -.1.8 3.6,,
TMO* 95.8 129.6 31,'2 25-9 7.8 3-35
Plastiq__4efprmatiorL- of supercooled a'ustenite
followed by conventional hardening and tempering
Card 4/4 treatment.

37728
S/l8O/62/6oo/oo2/ool/ol8
E193/E3,83
70 0
AUTHORS: Bokshtcyn VKishkin, S Lozinskiy, M.G. and
ISIn
Sokolkov, Ye*N* oscOW)
TITLE: Thermomechanical' treatment of a chromium-nickel-
manganese.austen:Ltic steel
PERIODICAL: Akad emiya 7 nault SSSR. Izvestiya..'Otdeleniye
tekhnicheskilch-nauk. Metallurglya 1 toplivo, no. 2.
1962, 15 2'1
TEXT: The, so-called -'-"thermomechanical treatment". (TMO)
consists essentially of.combining plastic-deformation at
temperatures above the recrystallization-temperature i-;ith
quenching under conditions.-precluding recrystallization of.the.
plastically deformed.material. The effect of this treatment on
thestructure and properties,.,of,various materials has already
beon studied by other irorkers Some additionil data on TMO
_01. austehitle steels are presented in'-the,present paper, with
particular reference to the properties.of-thete steels after
T1.110 to the ageing treatment' and to some characteristics of the
diffusion processes., The-43iperiments wereconducted on chromium-
Card

S/18o/62/000/002/001/018
Tkkermotmechanical treatment, ....
nickel-manganese austenItic -steel ?IA 481 (E148111 specimens,
13 and 60 mm in diameter$ the-former 150 and the latter 250 mm
long. The PlAstic-deforwatIon part of.TMO was effected by
rolling at 2.4 m/min in the. case of specimens 60 mm in diameter LA
and at 4-5,'7-5 and 130-i m/m:Ln inthe cas'e of,13 mm diameter
specimens 25 and 3050' reduction was-given in.each case.
R..2crystall:~Zation of, the 13 mm diametdr,'speciffiens was suppressed
by immediote quenching in a-water tank mouAted an the rolls
ilo--Sing, a time interval between completion of the rolling
opez-ation,-and quenching'amounting to 0.2 to 0.3 sec. Rapid
cooling o':C the- 60 mm diameter specimens was attained with the
aid of a'specially designed spraying-device. Preheating of
the test ~pieces for rolling Was done-in,air in. an electric
furnace, the-preheating-temperature and-time being 1 1~80 OC and
2 hours small (15 mm diameter)
F,-Is p actively - TMO of est.
pieces wAq.,.carried out after cooling them from 1 180 to'
0
1 100 C.Ir~,In the case.of large (60 mm diameter) test pieces
'h%io was ~ !, lied at- the preheating temperature and after cooling
pp
Card 2/8

S/180/6.2/000/002/001/01:-8
Thernomechanical ~reatme.nt E193/E3&3
1 000 0 C. 'A number of test pieces
50 1 100, 1 050 and
%-,rare Siven conventional treatment (water-qu~e~nching) to obtain
C01141-rol Speci pieces (whether
monaffor comparison. A41 tho test
quondh-hardene'd of subjected to TMO) Vere,aged at 68o OC-for
0 hours, .-after 14iCh they wei--e,-Siv-e an additional treaiment
0
of 10 hours at 799 C, followed-by a" -cooling so as to attain
~d
hardnes.S. corresponding to th,e ind'6nt ion diameter d i
Crr n
3.5 3.7 mm. In addition tostandard-tensile tests.at room
0
temperature, tests at 65o, C were carried ou 't under co-Aditions
of sliort and prolonged loading,%the latter (i.e.- cree .t2sts
b einZ'~ c.onduc ted under an applied stress of 39 or 43 kg/mm
'To study and compare the progress of diffusion processes in
m.atarial subjected to TMO or given the-conventional treatment,
the rate of,diffusion was measured by a radioactive-tracer
technique, entailing cutting a taper Aection'across the diffusion
region.
A, thin film. of IFe59 was electrodeposit 'ed on the specimens studied,
which were then given a 150-hours diffusion-Annoaling treatments.
at 800 0C In vacuum, aftiir which both volume and grain-boundary
Card 3/8

P/1,80/62/ooo/002/ool/o18
Thermomechanical treatniqni o*' E!93/E383
diffusion coef'Licie'nts were determined., Overall diffusion
coefficients were also calculated with the aid of the
absorption method. Phase-analysis was used.to study the effect
of hot plastic deformatio In on the process of carbide-formation
during aZeing.. Electrolytic extraction of the carbide phase
f 50%
from various,test pieces was carried out in a solutIon of
i _" e's i* I.also
hydrochlor a iac:Ld in methanol. The anode. r idues 'WreM,
examined by X-ray diffraction measurements. Preliminak'~r
e:zamination.of the microstructure revealed that, irrespective
of the roliiing sp ed employed during-TI-10, full suppression of
recrystall!2~atlon had been- achieved "' small. (13 ram diamoter)
test pieces only.,i, None of the TMO prTeedures used on-large
(60 mm diameter) test pieces had ensti;red suppression of the
recrystall:ization process. The results of standard tensile tests
at 20'and 650 OC, carried out on' small specimensi showed that
'r.-10 brouGht about a slight increase in UTS at 20 0 (from
1o8 - 114 icg/=2 ) but had 3to effect on the strength of steel
at 650 OC.. The variation in plasticity was somewhat different.
Card 4/8

T'hermomechanical treatment
S/180/62/ooo/oWbOIA18
E193/E383
Thus, as the'rolling speed during TMO increased, the elongation
of steel it room temperatu re decreased below that of specimens
i'leat-treatod in the conventional manner and then increased to
c-.zceed this value. The same applied to reduction in area which,
after TMO entailing deformation by rolling. at 13.5 m/min, attained
value of 33.200, i-e- 2500 hig-her than the value attained after
conventional treatment. The results of tensile tests at 650 COG
also showed a slight increase in elongation of specimens
subjected to TMO, although reduction in area of specimens
rolled at 13-5 m/min was somewhat lower than that of the control
zest pieces. The results of,accelerated creep ests conducted
on small test pieces under a stress of Ik3 lcg/mn, showed that
irrespective of the "conditions during TMO, the time-to-rupture
of the steels studied increased after this treatment by ~0-255')-
The corresponding increase for specimens tested undera stress
2
of 59 amounted to 600%. Metallographic examination of
sriall specimens showed that recrystallization during TOO had,
been completely suppressed in each of the specimens -examined.
This was indicated by the absence of-new small crystals which
Card 5/8

S/180/62/000/002/001/018
E193/E383
Thermomechanical treatmen't.
.-ere usually formed in recrystallized material along the
boundaries'-of the original grains. A-common specific structural
~cature of all specimens subjected.to TMO was distottion of
naaries which had assumed a~characteristic serrated
grain boun,
contour. distinguishing. feature of specimens rolled during
I
I'ViO at a sPeed of 41-5 m/min was well-developed sub-structure.
T! c fori:iatlon of sub-structure was associated with the for,-,iation
Of blocks (several tens'of microns in size) in the interior of*
.Wle grains:. The relatively large angular misalignment of these
blocie.s was' indicated by the ease with which the block boundaries
could be revealed by etching. No such clearly defined sub-~
structure was observed in,specimens rolled duri'ng VNIO at higher
speeds, although in a few isolated instances there was som6
evidence of blod'L- forrq'ation. The formation of the fine .structure
could be attributed to polygonization processes and subsequent
de-coratibn of tl~e'low-angle boundaries by the solute atoms and
second-phalso particlest Another specific feature of the structure
produced by TMO is tholfragmentation of grains, i.e. sub-divizilon
Card 6/8

S/18o/62/000/002/001/018
.i.iormo.,,,iechanical treatment Pl.q3/E383
Of srains into parts whose dimension are Commeasurable with
size of t*ae grains. themselves. , It would appear that
fra-:ier,tation is mainly a result of intensive tvrinninjggtaking
*)lace during hot plastic deformation. , As stated alre4e, none
of tihe T;%','O procedures applied to larg-,e (60 nun diameter")' test.
,)icces ensured complete suppression of recrystallization, the
extent of i-,rhich increased with depth ~so that an unrecrystallized
structure was obs6rved only in the very surface layers of the
ziat erial -In this case TMO had pract'ically no effect on.the
resistance-to-creep of the steels studied.. The results of phase
analysis showed that although the chromium-carbide-content of
sPecimens subjected to TMO.had inereased:considerably, it was
independent of the rolling speed employed in*the'course of this
treatment. The vanadium-carbide;content.of the material was
practically unaffected by TMO. -Finallyi the.results of diffusion
studles �nd:Lcated. that after TMO the coefficient of volume
diffusion of iron. in steel'at.800 OC increased fourfold. S:Lnce,
o---;in_c to a general increase in the diffusion mobility, diff:Lculties
Wor
i a encountered in determining the grain-boundary diffusion
Card 7/8

S/180/62/000/002/0'o"i/618
Thermomechanical-treatment ~E193/E383
coefficient the overall diffusion coefficients were measurerd
,0.\r the absorption method Comparison of the results obtained
f~x- tost pleces with dlf~erent structures showed that the
ov.erall diffusion coefficient for materials which had undergone
TI-10 was more than twice 'as high as that for specimens given the 11Y
conventional treatment. The general conclusion reached was
th-t in addition to the previously established strengthening
of-.'aact of grain-boundary distortion-caused by TNIO,.the beneficial
affcct of this treatment on the high-temperature properties of
stlocl was associated with an increase in the quantity of the
strengthening phase and, possibly, with refinement of the mosaic
structure and formation of slight,texture. There are figures
and 2 tables.
-SUBINITTED: October 11, 1961
Card 3/3

34841
S/i2g/62/000/003/002/009
Koo Elll/E335
AUTHORS; Bokshteyn, S.Z., Doctor of Technical Sciences,
Professor, Kjahkfn, 5jJ4, Corresponding Member of the
Academy of S-ciences and Moroz, L.1-1. , Cand-idate of
Technical Sciences
TITLE: Influence of carbon on the movement or grain
boundaries in the recrystallization of iron
PERIODICAL: Metallovedeniye i,termicheskaya obrabotka metallov,
no* 3, 1962, 8 13
TEXT- Lilcke and Detert.(Ref. l.- Acta Metallurg, v.5, no. ll,.,
1957) and Beek (Ref. 2 - Metal Interfaces, Cleveland ASM, 1952)
consider that there is a sharp drop in the speed of recrvstalli-
zation when the concentration of an impurity reaches some
critical value (about 0.01%).below the solubility.- Impurities
forming a second phase also retard the growth of recrystallization
centres. Using their radioactive-isotopes technique (Ref. 6-
"Zavodskaya laboratoriya, no.. 10, 1960) the present authors and
M.A. Gubareva have studied the influence of carbon on the
.behaviour of grain boundaries in the recrystallization of
Card 1A

S/129/62/000/003/002/009
Influence of carbon on a ... El11/E335
technical-grade iron. Carbon was chosen as an element
practically insoluble in alpha-iron; it is known to lead to
an increase in the activation energy of recrystallization of,
iron and, if present in quantities even slighly in excess of its
solubility, to prevent collective recrystallization, particu-
larly at 620 - 700 OC. Specimens were saturated with cat-bon
from donors at 700 OC for 2 hours. The behaviour of carbon
atoms at ivon-grain boundaries was followed directly during
deformation and subsequent recrystallizing-annealing.
Recrystallization was studied on specimens 10 - 15 and 50 - 709,')
deformed, -the first being in fact close to the critical value.
Autoradiograms obtained-before.and after deformation were com-
pared. From this and the titicrostructure the behaviour of the
carbon was evaluated. The sizes of.all grains increased after
deformation; heating to 550 0C failed to produce recrystal-
lization. but growth of alpha-phase grains occurred. Carbon
tended to move towards grain boundaries even when this meant0
going into a region of higher carbon concentration. At 650 C
recrystallization was almost complete, the carbon remaining at
Card 2/4

S/129/62/000/003/002/009
Influence of carbon on Elll/E335
the grain boundaries produced after heating at 550 OC.
Although recrystallization was practically instantaneous~ a
completely new fine-grained structure was produced. Heating to
750 OC produced growth of recrystallized grains and movement,
not always complete, of carbon to the now grain boundaries.
Recrystallization annealing at 700 OC for 45 min of specimens
after 130% deformation gave little change in microstructure;
0
carbon moved from the boundaries of deformed grains to those
of the new recrystallized grains. The influence of the alpha-
gamma transformation on the behaviour of carbon atoms located
at boundaries was studied in another series of experiments.
For this purpose specimensvere heated at 950 OC for 1 hour.
Completely new grains were produced, the carbon both migrating
to them and forming large accumulations of carbides. It -is
evident that the behaviour of impurity atoms located at
boundaries and forming interstitial solutions is very different
from that of boundary atoms of the base element; as shown
previously (Ref. 6), boundary atoms in iron recrystallization.
Card 3/4

S/129/.62/000/003/002/009
Influence of carbon on o Elll/E335
(Or polymorphic transformation) remain in practically the
-tame position; carbon atoms follow newly-formed grain
boundaries.
There are 8 figures and 1 table.
Card 4/4

S
alloy".
oushteyn.
jaronfint 14.13 -, B enura in raolybden ni-ye Sp'&vOv
I Molybd ova
Its. on 0
lj~djjjusl ractallurlo. 1911'ec
9 e Institut f thedePendence,11-1-
6Z, 1?" 1
the
ssspr jaT1 Y . (1),
nau no. to C tors - The
done
t r ) Jac Oys
I Gr" Vae vilner-al %q0 )n tw( I JAO all diffuslork
Soul. tsveiny'Ah .OrVing 0 j self-
(1, scribe' e%Pe ralneters 0' '-AO rate 0 . d estab
jDaper n kSD) pa, cedent CO the trie to 46 14540
rrhe i-diffusio ante . 13 between have
t. (.Z) the v latlon AS14, V
,XT1 _sel car et al d to
rrr, ir e V
Volurnetr 7 pretien to L. orrs Trans. -were use
'r 71-19; nr
.1 the contrib Sherbys -* in . clraens... JAO a I its
Ount 0, alloying a 0 D. t. 1 19154. pe T
arn .. intended as those which - I See -. 11'arge-gra . al jlu%- and high-
rl, 'Is ch as 6 no' * Liffuslork voc
-Wo .su Y- ' thodoiolk* totale dia:rn Is 7r. P-ight__
and r-reeps ij,&etalsi a Tne ;-, I.B-rnm 0 5450 of the
usally p.0 terial in the
. au-IS3 10 a d into all 0051) 7-r to , re cut out
;11 ca a volle h we - OC in a
lit T Ili% I
,?,B). est rar1b;-0-15aary - ?, 000
;;-~_ - 4-ratn
113 share 0 re-sraelted, frorn 0
- the ar a . srange aiaxn v 1 950- 1 attained 1-Z VaTn
reduce re V 'UUMOC., the alloy 14~rnra anneal at 9 ent!
we 17()0 1 specimens stabiliz"L9 all- S-pecim
7, at above valle ,_15-,hr I size
led lone-pa j to a the grain
annea . I'P 5er_te4
cylindrica sub U
and Were WheveU?O
ro -4 torr vacuWas
0
Gard 1/3
s/806/62/0001003/002/018
The self-diffusiOn Oj molybdenum - (height reduction 25%) to investi-
re so at 200 Lens W678 Olectr'"lly
Part of 'the specimens were upset on a p the mo. The specirr tive M099 i 1..I.,,-
cold working Or'. the SD of ith radioac n a
gate the effect of as activated w vacuum furnace
polished, whereupon one of their faces w I in a specia
nneal wap then performeo . The SD coefficient was
nic bath. Diffusion x _ 3 - torr and 1,720-Z,OOOOC'
galva _10 ratoriya, no.7v 1960,
(exploded view shown) at 10
two senior authors' method (Zavodskaya labo results: The
measured by the n the activity curve (summarized). Test --_STe-augmen-
828-830) based On the shift i asured (and tabulated) indicate an j~pprec
sion activation energy.
self-diffusion parameters me Zr on both the self-diffu , 00()0C the
ven small additions of nential term- Thus, at T above Zo
tation effect of e :
of the Mo and the factor before the expo the alloying, but at T below 1, 7000, in which
SD coefficient of Mo does not depend on SD rate decreases with increasing
the value of the activation energy is decisive, the
Zr content (numerical values tabulated). Even though antecedent cold-working de-
presses the SD activation energy of the Mo in Mo-Zr alloys, the activation energy
of upset specimen increases with increasing Zr content. Inasmuch as the diffusion
anneal of the deformed alloys was performed at a T substantially above their recry.-
tallization T, the latter was completeid in but a fraction of the anneal time and the
grain volume continued through an extended time in the ab;ence of
diffusion in the
any structural transformation, so that any observed lowering of the 5D activation
rgy of the Mo is regarded as a result of irreversible structural changes attribu-
ene
Card Z/3

The self-diffusion of molybdenum ... S/8061621000/003/OOZ/018
table to the cold-working of the alloy. The increase in activation energy during the
anneal is attributed to a healing of crystalline -lattice defects which previously had
served as "short-cut paths" for the diffusion; cold-working appears to firm up the
defects, thereby inhibiting the healing effect of the anneal. The relationship between
the SD coefficient and the activation energy is further examined and, in agreement
with G. J. Dienes (J. Appl. Phys., v.21, no.11, 1950,1189) and 3 Soviet authors, is
found to be exponential. The results of this investigation agree with existing
knowledge on the favorable effect of relatively small additions to Mo on its recrys-
tallization T, its hardness (ref. Pipitz, E., Kieffer, R.. Zs. f. Metallkunde, v.46,
no. 3, 1955, 187-194), and its high-T stress-rupture strength (Northcbtt, L.
Molybdenum. Russian translation, Moscow. Foreign*Lit. Publ. House, 1959,107-108).
There are 2 figures, 4 tables, and 16 references (11 Rus sian- language Soviet, 1
German cited above, 4 Engli oh- language of which I is *a Rue sian translation).
ASSOCLATION: None given.
Card 313

S/129/62/000/009/001/006
E071/E492
AUTHORS: Bokshteyn, S.Z.,,IDoctor of Technical.'S'ciences,Professor,
Bronfin, M.B., Engineer, 'Kishkin, S.T..j,-Doctor.of
Technical Sciences, Professor, Candidate
of Technical Sciences
TITLE: Grain boundaries on recrystallization
PERIODICAL. 'Metallovedeniye ittermicheskaya obrabotka-metallov,
no.9, 1962,.6-8
TEXT: This is a continuation of earlier work ("Zavodskaya
laboratoriyall, no.10, 196o). The behaviour-of W, Ni, Sn and
C admixtures present at the graiyt boundaries' dur.ing recrystallization
of iron (0.021% C, 0.0145% P, 0.01116 5, 0.6701isi, 0-070"a Al,,
u.o8% mn, o.o6% N!, 0-0339,06 Cu) was studied by autoradiographic
investigation and microstructural analysis. The admixtures,,
forming with iron substitutional solid solutions in the case of,
W1 Ni, Sn and interstitial.solid solutions in the case of C,
were introduc.ed by diffusion saturation at 600 to 7000C. The
recrystallizaition was carried out after preliminary deformations
of 10 to 15 and 50 to ~0%. The Ni, W and Sn were completely.
Card 1/3

5/129/62/000/009/001/006
Grain boundaries ... E071/E492
soluble in iron at all recrystallization temperatures
investigated and remained in their original lattice positions,
despite substahtial changes in the structure of the metal.
The behaviour of carbon atoms was substantially different:
above 7500C carbon passed from the boundaries of deformed grains
to the boundaries of now recrystallized grains. However, in the
initial stages of rAcrystallization (after 30 to 45 min at
650 to 750*0 carbon atoms remain at tho boundaries of thiu, iIIIL,,IL
grains and boundaries of the new grains remain free from carbot,l.
The possibility of "heredity'l, i.e. preservation of the initial
structural and concentration non-uniformities in recrystallized
metal was demonstrated on a molybdenum allay (0.545/o Zr, 0.00%.", Cr,
mooN Ti and 0.0110% CY. A thin layer of tungsten 185 -;.ras
electrodeposited on the surface of a flat specimen of the deformed
alloy, submitted to a preliminary annealing at 17000C. The
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-boundaries
of the newly formed grains but also a preferential penetration of
'Card 2/3

S/129/62/000/009/001/006
Grain boundaries ... E071/E492
the W185 along those sections.where old grain bourfdaries were
passing before recrystallization. The velocity of diffusibn
along the old bound4kries was lower than along the now boundaries,
nevertheless it was noticeably faster than-volume diffusion.
The results confirmed tha.-t within the grains the process of grain
boundary migration does not produce as high *concentration of
defects as is produced at the'beginning.and at the end of the
boundary migration. Therear.e 6 figures.
Card 3/3

TUMANOV, A.T., Flav. red.; ITYANDT, A.Ye., red.; GARBA'I?_,M.j,4.-kaW-,.
tekME.~"uk rr*dsj.:fXMGIN.,-V,A,,."
- , redsj~~ZAYMOVSW. if
redq_~M-_Xpa~p red.; KISHX=A-.4ATI=,, S.I.&# daktor.
tewA rjw"'. PAN t- Jrind6 -tekbin nnk -red*;
~7- EMNI, -.Be. - - f .9
d.; SAZIW -P#i red.;
R 12.4k. dcjkt446C~ YAuk, re Ip -5,;
M -:4.) ~ - ~.. I -
SKLYAROV N. Aor.'tekhn.nauk, red.; FRIDLYANDER., IX,,
doktor teldlli. red.; SHUBNIKOV, A.V.,, red.;. SHMMBINA,
V.V., doktor geol.-miner. nauk., red.; SHRAYBER, D,S., kadn,
tekhn.nauk red.;*MMEW S.V. kand., tekhn.nauk
Y f 1 0 , red.;
NOVIKOV ' A.S.., doktor khoze nauk,, red.; KITAYGORODSKIY,, I.I.,
doktor tekhn. nauk,, red.; ZHEREBKOV, S.K.p kand. tekhn. nauk,
red.; BOGATYREVj P.M., kand. tekhn. nauk,, red.; BUROV, S.V.,
kand. tekhn.nauk,, bred.` POTAK, Ya.M., doktor tekbn. nauk"
red.; KUKIN ~G.N.v~doktor tekhn. nauko red.; KOVALEV, A.I.,
.kand. tekhn,, nauk,,.red.,- ZENTSELISKAYAp Ch.A., tekhn. red.
[Building materials;*an encyclopedia of modern technology)
KonstrulktsionrWe mterialy; e,ntsiklopediia sovremennoi tekh-
niki. Glav. red..Tumanov,, A.A., Moskva, Sovetskaia entsiklo-
pediia. Vol.l... Abliatsiia - Korroziia. 1963. 416 P.
(MIRA 17:3)
1. Chlen-korrespondent AN SSSR (for Kishkin).

(Strains and stresses) (Diffusion)

....... ...

1ABD -JD- -- - ---
11 J',
V
_Me SION; M:
8/019-9/63/000/005/0040/00
44
-1 A
PO: o-_ 0
_AUM01 i` To ishov A,
sokshtt6ii, SO: Z Lyak zi~
solov~reva)T 77
_
.
TLE
ial
d
T
t
la
t
orme~
: - A

o
s
ic
ef
I
_p
gip al
~~
-0,8. 'a metall
~~OOUHCE: 0v, hob 5 06
c
ji~mintl P'ligh t4a~eriatiwe low temperature,,
o-l -tit
he a -heat resistant loy anium alloy, aging, m6chaaical
propertiea.- rqt~re li e-

--A re

4
ABSTRACT View of-,fA3a~ha the~echanical treatment of, i'steeii
r#porzs on-
.
l
,
ii

-
---
.and'a
OYS efte s F
teneficial at on
rupture tie
ogth --

to a~ t cess q
only cer. ain tempex a dE~h6i~'-6imperatures the diffusion,pro

t, - wMch Cause softe --pio `jj;t
ni#g a]~,.conzi er ly 1xigber rate-tham-in 6onventi6i
ab
i treated a1ioys o-i -,For,- 13istanadif- an"Aii-br'-V-~b-Ti-41 alloy
'

"
'and aging hadla
8 4bi
r~qptur6life at.-
lower than conventionally tivate
.
p
A
alloys, although'-Its tensile" strength.'was- -25% higter. At lower service tempera-
-b-ase -base alloys
(559C.forl jgiv a~lov, and"450
to 500C`for Ti THr'greatly.
.
iucreases.~ cr ep-- strength and*iupt life es eciany vhen.combinedwith agi
e Pg..
p

.ACCESSION NR:- AT4023931 8/2659/63/020/000/0082/0086
..-AUTHOR: Blistanov, A. A.; Bokshteyn, S. Z. Gudkova, T. L Zhukhovitaldy, A. A..
Kishkin, S. T.
TITLE: Investigation of the influence of stress on pore formation
V1
SOURCE: AN SSSR. Institut metallurgii. Issledovaniya po zharoprochny*M splavam.
v. 10, 1963, 81-86
TOPIC TAGS: pore formation, high temperature stress, external stress, strain,
cracking, brass, .alloy structure
ABSTRACT: Pores arise from the coagulation of vacancies produced in the crystal
lattice by high temperatures and the effect of external stress and plastic deformation.
There is very little information In the world literature on the various factors affecting "J.,
pore formation, and most of the work which has been done is qualitativo in nature.
There has been little theoretical work with a quantitative approach, and no experimental
work, despite the importance of the subject. The present investigation considered the
maiwlaws of pore. distribution, the influence of external factors on pore formation, the
relationship between pore formation and the structure of the specimen, and the mec am
hani
1/3
LCard

ACCESSION NR: AT4013931
of-the-formation of pores and cracks in the presence or absence of external factors.
Experiments were carried out on 'K *-brass annealed for 50 hrs. at 800C, clectropolished,
heated by diffusion and then subjected to density determination and examination of the
microstructure. The results corroborated the main laws of pore distribution near the
sample surface, but showed that the distribution often differed from that predicted on the
basis of the laws of diffusion. A theoretical analysis is carried out of the nature of pore
distribution at varying depths in the specimen, yielding a calculated curve with a maximura
pore density which agreed well with the experimentally determined curve for brass. In
polycrystalline brass, pore formation takes place primarily as the result of the -limited
diffusion of zinc, with volume diffusion playing an increasing role at high temperatures.
External stress was found to play an important role in accelerating pore formdtion and
development along the grain boundaries. Under the Influence of stress, the energy
of activation for pore formation was increased to 26 kcal/gram-atom. it was thus of the
same order of magnitude as the energy of activation of diffusion of thle volatile component
along the grain boundaries. It Is suggested that at high temperatures cracks develop
mai-I - an tbe result of destructlon of material remaining between the pores, while at low
raw res Oic principal process to pore coagulation. 7be role of impurities in ppr
fonr;;:~.11ha Und Olair otfoaL In determining the pore d1otribution In pointed out. A
'
-thcorc.
;cal evaluatlon of the role of7the grain boundaries in pore formation, using the
2/3

ACCESSION NR: AT4040405 S/0000/64/000/000/0026/0035
AUTHOIU Bokshteyn, S. Z. Bronfin, M. B. S _T
TITLE: Surface and bulk diffusion of tungsten in molybdenum
SOt1RCE: Protsessy* dMzU, struktura, I evoystva metallov (Diffusion processes, structure
and properties of metals); sbornik statey. Moscow, Izd-vo Mashinostroyeniye, 1964, 25-35
TOPIC TAGS: tungsten, molybdenum, surface diffusion, analysis, bulk diffusion analysis,
autoradlographic analysis* method, activity curve analysis method, diffusion coefficient,
diffusion equation, diffusion activation entropy. vacancy formation energy
ABSTRACT: The radioactive isotope W185 was electroplated on fine-grained flat plates of
Mo for autoradlographic analyses of bulk diffusion and surface diffusion, as well as on coarse-
grained cylindrical samples for bulk diffusion analyses based on displacements of activity
curves. Diffusion coefficients were determified for all samples (see Table 1 In the.Enclosure)
and further processing yielded the equations
D 3.18 OW [-(11 CM2/sec
2900 1000)/RT,3
card

ACM.S.SION Nt: AT404040 5
MICLOSUREt
01

Table 1. Diffusion coefficient in cm for diffusion of W in NO.

Z
of diffusion
Temp.

annealinsr in *C
1700
1750
1830
1850
1880 1900
ac-
Bulk diffusion -12 _11
, 5.8x10 1. 1xio
tivity curve dia-
placement analysis (47.5) (109.6)
Ora.)
Bulk diffusion,
9 12
Oxio 12
2. Ox1O 12
8. 9xio 41
1. 2x1O
autoradiographic
analysis (hra. ( 112) (108) (103) (99)
i Intercrystalline 5.4x10 -9 LWO -8 2.OxlO-8
diffusion

cc"
3A A

-Kccmro
SNIGLOSTREs 02

T ,

1956 2100
IXIO 25xlO
1
.
(59) (24)

Tel"
ILL

all
cc d

8/6000/64/000/000/0040/0051
ACCESSION M: AT4040407
AUTHOR: Bokshtsyn, S. Za; Dronfin, N. L; Kishki S. T.; Marichav. V. A.
N_
TITLE:' Investigation of conditions at the grain boundaries in so-tybdenum and
-,"its alloys with zirconium and thenius by the method of-internal friction
SOURCE: Protaessy* diffusLL, strukturs L evoystva metallov (Diffusion processese,
structure and properties of stitals); aboralk'statey. Moscow, ZIA-vo Maskino-
stroyeniye. 1964, 40-51
TOPIC TAGS: molybdenum, molybdenum alloy. molybdenum grain boundary. molybdenum
rhenLum. alloy, molybdenum zirconium alloy,,chenLum, zirconium, internal friction,
stress relaxation. alloy diffusion..
ABSTRACT: The machantSIR of'stress relaxation at the grain boundaries in pure
metals is known to be affected by the,presence of alloying elements, but precisely
how is still unclear. The study of internal friction, based on measurement of
the forced oscillation dampening of a polycrystalline specimen is a sensitive
method for investigation of the structural conditions of a metal generally, slid
particularly-at the.Srain boundaries. The present authors experimented with
spectmene of. 99.98% pure sintered malybdamum;.s, No --Zr alloy castaLaLeg 0,= Zc,,
A

ACCUSION M AT404M7
6.ws% ci-O.'006% 09,, and 0.0007% K2; and Na+30%'Re. The spectimmas were subjected!
to torsional oscillations (0.3-0 4 cycles/see.) at various ml caturen Is a rd
up
K of about 20 -~ 1000~ 0 after swam I f -2 46 t' tesiparatuces up to 2000C. Ow test
installation we originally developed by~V. D. OsvenskLy and Is diown-acbemstLealli
In 6odLfLed form, in Fig. I of the ffaclosure. The activation miergy It of 'intermal
i frLctLoo,was.detendbod frm the expression
jOS 9-L Slos All 0.4346 IT
under the assumption that to r,-e swconst. :1FLg. 2 of the Enclosure abows%tba
Q- f0
temperatuto dependence a. - C19- 3 mateciaLe compared. The results showed
that the boundary relaxation.boaLus to grow at different temperatures In different
alloys. - Thus, this temperature is 700C for the No-Ra alloy and about 6M for per I
molybdenum or Ko+O.L3% Zr. Beginning at 700C, the highest L*"L- of Internal
friction is shown by unalloyed mlybdenumi; the lowest - by Its alloy
rhaniumi. If the internal friction along the grain boundaries depended
Only
on.the activatLon.amergy,Lt sbcold be maximl, in the KO.ZC all!jy, snd "t
2/S
1: 1.2 "V, I.,

;ACCESSION HR: AT4040407
h
.pure molybdenum. A mechanism of boundary relaxation Is therefore suggested whic
is connected with a migration of Interstitial solutes such as oxygen, carbon and
nitrogin. This migration requires less energy than the displacement of the dif-il
fusionally more-inert atoms normally occupying the nodal points In the lattice.
s cou explain the relatively,low activation energy of Internal friction-f6und,
at the grain boundaries. Qualitatively, the Influence of dlffusional replacement
components can be explained by the mutual Interaction between these components an
i
the migrating atoms of penetrating components. as well as the ability of the re-
placement components to sitar the structural imperfections In Intergranular zonese
"The authors express thanks to Ye..M. SavItskly and M. A. Ty*lkIna for supplying
the Mo-Re alloy." OrIg. art, has:.-5.figure* and 4 formulas.
ASSOCIATION; l6one.
SUBMITTED ~ENCL.* 02
090"A3
sue CODE: HK NO REF SQV*,- 003 005
OTHER:
or 3/5

ACCESSION NR: AT4040412 S/0000/64/000/000/0074/0094
AUTHOR: Bokshteyn, S. Z. Kishkin, S. T. Moroz, L. M.
TITLE: Investigation of the conditions of the grain boundaries during recrystaluzation Of
-iron and its alloys
1 SOURCE:. Protsessy* diffuzil, struktura I svoystva. mettallov (Diffusion processes,
structure and properties of metals); sbornik statey. Moscow, Izd-vo Mashinostroyeniyet
1964, 74-94
TOPIC TAGS:* iron, iron alloy, steel, tungsten steel, carbon steel, steel structure,
grain boundary, redlystallization, tron'yntorostructure, oarbon diffusion, tungsten
diffusion, tin diffusion, nickel diffusion
ABSTRACT: There'are still x aspects of the mechanism of recrystallization
unclea
suchas the nature of the~reconstruction of grain boundaries, the formation of new gridns~.,;
and.their subsequent growth*, -the influence of impurities, and the role of diffusion.- The
present authors Investigated recrysfallization of Iron in specimens previq~sly 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..!
' t 1A

ACCESSION NR: AT4040411
showed that atoms of soluble impurities (nickel, tungsten, tin), like the atoms of the base-
'metal, practically remain at their initial locations despite significant changes in the micro-
structure of the metal. Prolonged annealing at recrystallization temperature (78 hrs. at
700C for iron with nickel; 30 hrs. for iron with tin; 213 hrs. at 750 C for Iron with tungsten),
heating at temperatures above the A3-point, or high-temperature annealing (30 min. at
1200 C for iron with tungsten) did not cause~_;ttomlc migration of impurities from the initial
locations toward the boundaries of the recrystallized grains, regardless of the degree of
prior deformation. During recrystallization, atoms of impurities which vmre loceed at the
grain boundaries and formed part of the solid solution by penetration showed a substantially
different behavior than atoms of base-metal 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
the migration process be determined and compared with the activation energy of the dff--~
fusion process of carbon in iron. Orig. art. has-. 25 photomicrographs and 3 tables.
ASSOCIATION: None
I.- _
CWrT 3/4

ACCESSION N14 AT4040413 S/0000/64/000/000/00.99
/010
AUTHOR: Bokshteyn, S. ~Z; L. M.; Chaply*gIna, V. S.
TITLE:. Structure imperfections of metal following recrystallization
SOURCE: Protsessy* diffuzil, struktura I svoystva. metallov (Diffusion I processes,
structure and properties of metals); sbornik statey. Moscow, lzd-vo MashInostr0YeniYe,!"*.
-1964, 99-109
J.
TOPIC TAGS: metal structure, metal diffusion, diffusion. permeability, metal re-
crystallization, iron, tin, tungsten, carbon diffusion
ABSTRACT
Many of the th
properties and processes occurring in metale'depend upon e
degree of structural perfection. However, it is not clear hoV and under what CUM- I-
cir
stances structural defects arise or disappear.. In some cases, it has been possible to
achieve 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'.,
re
*assumption can be made that in regions where grain boundaries have been located befo
ec
~r rystallixatiomc, preaer4ation6f thiioi0ffic- state is possible, Le., there is a possibility:,;
Card 1/3'

ACCESSION NR: AT4040413
of "hered'i In the pkesentipaper, the authors investigated the beredity of metal strue
ty
coplo
ture during recrystallization and grain growth, using autoradiographic and micros
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
s. Iron was anneal at 1250C for 9 hrs.,
purity and the recrystallization con itior
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. 1 hr., followed by
heating at 600C for.1 hr. In the presence of radioactive carbon. Measurements of hardness.:',
and C14 distribution demonstrated that diffusion is affected by recrystallization temperature
and that the residual effects of previous cold working can remain after application of the
common types of recrystallization. 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. i i
Ii f
It is possible that, in the latter case, the alloy fails along the boundaries of original
/3
-------------

ACCESSION NR: AT4040413
grains which were metallographically undetectable. The question of the influence of
various impurities on the defectiveness of the original grain boundaries thus gains con-'.
I,,. 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 td assume that
the detrimental influenve of Impurities can be'reduced by applying suitable rec.rystallizationj,.~
conditions. Orig. art. has: 7 figures and I table.
ASS
OCIATION: none
SUBMTTED: 09Dec63 DATE ACQ; 28May64 ENCL: 0
SOV.- .002 -OTHER: 0001-
SUB CODE: MM NO REF

ACCESSION NR: AT4040417 S/0000/64/000/000/0133/0146
AUTHOR: Blistanov, A.A.; Bokshteyn, S.Z.; Gudkova, T. L; Kishkin, S.t.; ZhukhqvitakiY,_~"__'_'
A. A.
TITLE: Pore formation and rupture at high temperatures in relation to stress and me.tal
structure
SOURCE: Protsessy* diffuzii, struktura i svoystva metallov (Diffusion processes, structure
and properties of metals); sbornik statey. Moscow,# Izd-vo Mashinostroyeniye, 1964, 133-146
..TOPIC TAGS: alpha brass, nichrome, nickel based alloy, alloy-pore formation, volatile
constituent diffusion, grain boundary effect, stress effect, metaflitructure effect, high tem-
perature failure, metal failure analysis
~ABSTRACT: This study concerned the kinetics of pore formation, as well as'the effects of
stress, temperature and structure of the metal on such processes in relation to fallure of
the metal at high temperatures. Sheet samples of alpha brass (32% Zn and 68% Cu; annealed
50 hra. at 800C and 0. 01 rnrn Hg) and a Nichrome alloy (20% Cr, *80% Ni; pre',Iomogenized
Card .1/2

ACCESSION NR: AT4040417
50 hrs.. at, 1200 C in argon) were polished electrolytically, then homogenized in a vacuum
(residual pressure 0. 001 mm Hg'temp. 500 - 1250C, volatile component distillation) under
-stresses varying from 15 to 120 kg/c or unstressed. Results obtained with the brass
samples indicate that pore formation is initiated due to evaporation and the accompanying
-diffusive migration of constituents. The effect of grain boundaries is not apparent in the
inifial stages, but becomes clearly pronounced as the process continues. Pores form earlier
as temperature rises. The presence of stress accelerates the process and the effect of grain
:boundaries rises sharply. The process is completed by cracking and rupVAre along the grain
;boundaries. - Pore formation was absent in unstressed nichrome, while stressed samples
showed significant porosit-j, cracks and eventual failure, mainly along the grain boundaries.
-*Other experiments indicate that hetero(yeneity of the material significantly affects patterns
of pore distribution. It is concluded thkt similar studies will permit physical analysis of
metal failure at high temperatures. Orig. art. has: 4 graphs and 8 photomicrographs.
ASSOCIATION: none
,SUBbUTTED. 09Dec63 DATE ACQ: 28May64 ENCL:. 00
SUB CODE: MM 003
'NO REF SOV: 003 OTHER:
Czrd 2/2

ACCESSION NR: AT4040418 8/0000/64/000/000/0147/0161'
AUTHOR: Bokshteyn, S. Z, Gudkova, T. I. Zhukhovitakiy, A. A. Kisbkin. S. T.
TITLE: Effect of preliminary deformation on pore formation
"A
SOURCE:' Protsessy* diffuzil, struktura i svoystva metallov (Diffusion processes, structuis
and properties of metals); abornik statey. Moscow, Izd-va Mashinostroyeniye, 1964, 147-151
TOPIC TAGS: alpha brass, Oore formation. preliminary deformation effect, high tem'per
effect, metal evaporation, allay failure
ABSTRACT: Cylindrical samples (h 10 mm) of alpha brass (36% Zn, 62% Cu) were ant.
nealed for 3 bra. at 800C in an argon atmosphere.. then pressed at room temperatt
deformation levels of 3-5%. 15-20% and 55-60%. The effect of preliminary deforniation on,
evaporation was evaluated from changes in sample weight during subsequent vacuum ho
nizing (4 hra. at 700, 800 or 850C). It was found that preliminary plastic deformation In-
[creased the rate of evaporation, as well as the number and site of pores forming at
L temperatures. The effect was most pronounced at deformation levels of 10% or less OW
to

ACCESMON NR: AT4040418

t
d
J
h
O
t
I
i
@ 4
a
h 04.
as
ncrease
.
r
.
higher levels or as
ompor*W"
g., ~Lr
decreased a .
s.
gr
p

ASSCCU71ON: ame

DATIC ACQ: 28MAy"
SUBMWED.-

NCU. 00 -gv

-000
ir BOV OTIJZIU 000

:
ISUB CODE: MM, NO It ~R

-7

ACCESSION NR- AT4040419, S/0000/64/000/000/0155/0167
AUTHOR: B L.
okshteyno So Z.:
Ical properties of Cu,.Ni and Co whiskers
TITLE. A. study of, the mechan.
SOURCE: Protsesby* diffuzit, struktura'i evoystva metAllov (Diffusion processesp structure
and properties,of metals); sbornik statey. Moscow, lzd-vo Mashinostroyeaiye, 1964P 156-167.,
tal
TOPIC TAGS- copper whisker crystal, nickel whisker crystalp whisker crys
whisker tensile strength, whisker structural defect, whisker aftoying effect, W
effect, whisker m1orocryStalline dislocation, selective etching OFocedure
-(length -1. 5-3 mm, diMneter = 2-15p), grown,by
ABSTRACT: Whiskers of:CuV M and Co*
hydrogen redaction of anhydrous haloid salts, were tested for tensile strengthin relation to
crystal diameter and orientation of Ito long axis, as well as for variation in strength I
and the effect of alloying (diffusive'saturation of Cu with Ag) on mechanical properties.
Selective etching was used to expose microorystalline dislocations in the Cu. The results
indicate substantial divergence in relation to diameter, especially for very small diameters,,,,'
of 2 - 3 ji.
_~mpirlcal relationships were derived between diameter and tensile streng*'...
Card
_2

ACCESSION NR: AT4040421 S/900/64/000/000/0177/0182,
AUTHOR: Bokshteyn, S. Z.;. Glazunov, S. G.; Yemel yanova,,.T. As;
'Kabanov, Yu. N.; 4_tik_h n,, 5T,; Mirskiy* L. M.
1,!TITLE: Thermomechanical treatment of titanium alloys with $-structure,
;SOURCE: Protsessy* diffuzii, struktura.i svoystva metallov (Diffusion.,,
structure, and properties of metals); sbornik statey,
:'Moscow, Izd-vo Mashinostroyeniye, 1964. 177-182
TOPIC TAGS: titanium alloy, beta -structure, mechanical property. the rmo,-
mechanical treatment, thermomechanical treatment effect
1ABSTRACT: The'effect~of thermomechanical treatment on the mechanical'.:
properties of $-titanium alloys VT15 (3.76% Al, 7.60 Mo, 10.7% Cr) and"
V-120 (US alloy, 3.1% Al, 11.6Z Cr, 12.6% V) were investigated. Al-
loy apecimens were hold at 760C for 30 minutes. then.rolled,with a.
~reduction of either 10 or 45Z and immediately queqched (high tempera-,.-
1
1ture thermomechanical.treatment, UTTMT) or they were cooled at 350C
held for 2-3 minutess. rolled with.a reduction of 110 or 40Z., and
Ca-W 'It 2

,ACCESSION NR: AT4040421,
!immediately quenched. In both cases, quenching was followed by aging!-
at 450C for 25 or 50 hr. The'.machanical,properties of differently
wn 'Table 1 6f the Enclosure,
1!treated alloys are sho In stress
2
,,.rupture tests Japparedtly at 406C) under a stress of 100 kg/mm , the..I-.
alloy had a rupture life of 13.5-15.0 hr. 'elongation of
v; 17.2-19.0%, and a reduction of. area of 49.0-51.5% after HTTMT.
;~The V-120 alloy similarly. treated had a rupture
life of 97-100 hr.
i;, orig. art. has: 5 figures- 'and 4 tables.
ASSOCIATION: none
SUBMITTED: 09Dec63. ATD,--PRESS: -3049. ENCL:, Ol-'
-001
SUB CODE: MH NO REP SOVi 000 OTHER.:
j a Fd
2/2

ACCESSION NR: AT404042,2 S/00001641000/000/0183/0167
1AUTHOR: Bokahteyl, S. Z.; Kishkin. S. T.; Moroz, L. M.
TITLE: Effect of thermomechanical treatment on diffusion nobility,
SOURCE: Protsessy* diffuzit, siruktura i evoystva metallov.
(Diffusion processe , structure and properties of metals); abornik
.Statey. HC I-vo Hashinostroyeniye, 1964, 183-X87
I
~VOPIC TAGSt thermomi-chanical treatment, diffusibn mopility,
41ffusion coefficient, fine structure, diffusion mobility deter=in&-1~:':1'_".!
tion, thermomechanical treatment effect
ABSTRACT: The diffusion mobility of iron in austenitic steel E1481
and E1437B alloy were investigated after conventional heat treatmen" _'
and after thermomechanical treatment (TMT). The parameters.of the. X.
latter treatment were: 1080C - temperature of deformation; 28%
reduction;-and 13.5 m/t~in - deformation rate., The diffusion nobilitil.-
was determined by the method of tagged atoms in combination with,
microstructure analysis. The specimens were electrolytically coated"
_L3

S_
CCE SION HR: AT4040422
A
with a thin film of ri0ioactive FeS9 and annealed in a vacuum
furnace at SOOC for 150 hr. After annealing, the dAffusion coef-
'Pe and graim, boundaries.
ficients were calculatid for grain volu, d.
Table I (see enclosure) presents the repults obtained.. IThus, TMT
changes not only the conditions of the grain bound4~ries, but of the
grain bodies as well. ,'The increase of Oiffusion mobility is pro-
served even lafter annealing at higher temperatures, re,
'~temperatu
of recrystallizatLon). The Lncrease of diffusLon mobility producedt
by TMT limits the applicability of this method for heat-resistant
alloys, TMT could bo'beneficial, however. for alloy worktng at
relatively low temperature. Orig. art* has: 4 figures and 2 tables,
ASSOCIATION: none
'09Dec63 ATD PRESS: '3072. ENCL
SUBMITTED: 01.
NO REP SOVI 001 OTHER:
SUB CODE.% HM 06

ACCESSION NRI AT4040422 ENCLOSM i
Table 1. Iron diffusion ebefficients
D-10 cm /see on grain boundaries Dgr
and in grain bodies Db of alloys E11437B
and E1481 at 800C
N
ConventL-onal
heat treatment TMT
Alloy
DgT7 Db Dgr I Db
E1481 ;0.62 4.6
2.8
E1437B 0.87 3.5 1.7
Average diffusion coefficient
E1481 i'l.4
3.0
E1437B 190 1.3
Card 3/3

A
i -XCCESSION NR: AP4037065 S/0129/64/000/005/0021/0028,
AUTHOR: Drozdovskiy, B. A'*; Pevzuer, Lo H*; Tarantovat A. S.;
Fridmanp Yao Be; KLshki
n p,
TITLE: Effect of carbon content on the tensile strength of structural-,-,
steel sheets
J.
SPURCE: Metallovedeniye L*termichesiaya obrabotka metallov
n6_.. 5, 1964, 21-28
1
TOPIC TAGS: high strength steel, superstrength steel, medium alloy,!~,
steel, VKS-l steel, solid fuel rocket, rocket case, rocket case
material, steel notch sensitivity
ABSTRACT: The effectsof carbon content, melting conditi,oneq an-d he it
treatment conditions (primarily tempering temperature) on the strength
and ductility (in conventional tensile testi and under biaxial ten-
sion), and notch sensitivity of two superstrength steels VKS-l and'
[AIS114137-Co -are investigated. Four grades of VKS-1 (0.30, 0.399
0.45, or 0.53% carbon; 0.89% manganese; 1.2% silicon; 1.87% chromi-
um; 0 72% nickel; 0.49% molybdenum; r.05% vansedium; o.= sulfur;-. and 0.008Z
-Card 1)4

- ----------------------------
F-7
ACCESSION NR: AP4037065
phosphorus) were melted in an open atmosphere induction furnace*
-0.84% manganese, 1.02% silicon, 1.32%
The 4137-Co (0.40Z carbon,
as,
chromium, 0.36% molybdenum, 0.19% vanadium, and 1.1% cobnlt) w
melted either in an open atmosphere induction furnace or in a con
Both steels were rolled into
sumable electrode vacuum',arc furnace.
sheets I mm, (V1-'-S-1) or 1.5mm (4137-Co) thick. Special care was
taken to prevent surface decarburization. Tests revealed that
tensile and yield strength of VKS-l steel increased steadily with
increased carbon content up to 0.45%. Steel with 0.45%,carhon tempered
at 150C has a tensile strength of 240-245 kg/mmz hut low ductility
-it 220C the steel had-
and a high notch sensitivity. When tempered .
-230 kg/mm2, yield s trenpth of 180 kg/mm2
a tensile strength of 220 and
elongation 6.5Z. Further increase of carbon content brings about
premature brittle failures. Elongation remain's almost unaffected
by increase of carbon content from 0,30 to 0,45% but notch sensitivity..
increases very sharply, Under conditions of biaxial tension the
strength of VKS-l increased with higher carbon content only up
to
0.397.. With 0.30-0.39% carbon the fracture is ductile and th a
strength is higher than that in uniaxial tonsion. A0 the car 01ft
content is increased to 0.45% the fracture becomes brittlel, the
i, ard Z/ 4

---'ACCESSION NR: AP'4037065
q >th drops and goes b low the.level noted in uniaxial tens Pne,
s reng
Generally, the maxima on the strength-carbon content or strength"
tempering temperatuxe curvoes for biaxial tension do not coincide with those
for uniaxial tonsion.but occur-at carbon contents and tempering
at which the strength in-uniaxial tension amounts to about,-
temperature
2
kglmm The behavior of 4137-C o steel followed a similar pattern~,1'4
IIt was found, however, that- vacuum are melting improved ductilityp
especially in biaxial tension, and lowered notch sensitivity. ;No
e a
'I brittle failures were observed even at temp ring temperature a low
Ias 150C. -No correlation.between the strength in biaxial tension
nsion was found in either
and any characteristics in uniaxial te
steel& It is concluded :that the problem of improvement of stru-c 1
tura
strengtn is closely related to the prevantion of brittle fracture
at higher uniaxial strength.
This can.be achieved by complex alloy
1ing with a minimum segregation of componentq; improved metallurgical
procestes'ensuring higher 'urity of metal,* control of solidificationi."',-
p
processesto prevent microsegregation and improve the strength of
interdendritie boundaries; and finally by thermomechanical treatment!!,
with a maximum graLn-refinamento'
Card 3/ 4

L Ig-1-4-116-65 EWT(m)/*EPF(n)-2/T/W(b) Pad/Pu-4 ASD(m)-3 Mvl/JD/W/JG
.9/2535/64/006/i$
S 3 ION- ~NR: :-:AT4%k47
ACCL
AUTHOR: Kishkin, Se Tb(,130~itor of technical sciences)t KI La A. A,
(Candidate oF-Mlmtvat sciences)
7_7~~,
T-ITLE-v- EfFict----u 'dho-ie
-t.-: b_Vjj thda till go on properties of heat
Fallove
SOURCE t Moscow Avi'ats iris i tut -Trudy*, no* 158, 196 4
11saledovaniya struktury-* i sV*Y6t:V,zhproprochny*kh aplavov (Studies
ion the structure and properties of heat-resistant, alloys). 14-19
TOPIC TAGSt-., heat base alloy,'91437 alloy,
nickel alloy overhadtinsp -cold *farked alloy property, overheated
cOmPlex alloy property, nickel alloy heat resistance, nickel alloy
rupture life
14
ABSTRACTt The' effe -6 art overheatings an the U431'A,eat-resie-1
-tant nickel-b I
_jLtqjH Nimanic 801 has bean studiedl=t was found
~that overheating of a licat-treated (annealed dnd aged) alloy to tem-
1peratures up
__~d 800C has no affect an hardness, but at 900-1300C the
card 1 3

77
-1641&65
V
'Ad-C"SI& Iffu --AT40-4-74750--
sih-a-rptyr-, f
"M proximitel 300 1tv, to 155, -Lao n~~7
f i rs t0 See..- 01; ~a -.-I di
IdO&*v4xpqFs-ur nA tt e.or~;qo ad tL*4, 1
AX
A~ . P
-The -1006-1
al *--E-f t _706.0- ex 8 re
d: increaseg uct ~tyv
an II L' ~thts:,Ls apparently due ~to the ... dissolis Uum -
of particles--of -the -stteligtfienift:: phai e- at"d 'their coagulationa S r -a'8
rupturt tasts- at TOOC under A stress of 36 ka/MM2 showed that specimens.-
exposed to SOOv 900# or IGOOC,. for 1000 see had a rupture Life af-
1.40, 24, and 16 hr. respectLvelyteampared to 100 hr for specimens
which weee not overheated@*, 'Ductility of overheated specimens was
erheatLng to 300C -shortens the
,greatly increased. Thus, even ov
rupture life of the altoysalthoughtte hardness remains unchanged. 0
ithe contrary, overheating of the a-traLa-hardened alloy prolongs Les i
irupture life, The effect of short overheatings in both aging and
Inonaging 'nickel alloys can be minimized by the addition of chromium,
;tblyb-denum,_ ahd tun-astilft Whi-ch -19Ubst&UUkktY'9btftgthen solid aolutiort.,
,:especiAlly in the presence of phases which strengthen the alloy durtn
I
'aging, TbIk ZZAdgth dCtheZT437 alloy to which cob VI; -bdenum;v~,
Altt OLY
landim=&" been added-begins to decrease at higher temperatureal
~than that of the same 11LOY without these elaments. A complex heat
iCOTA 2/3

OTHERt-
-S IM, CODE
ILS doo
RD~ 2
/2

L 41225-6'5
'ACCESSION NR: AT4044753 S12535f6410OOfl58/Q035/Ga2
(Candidate of technical a 'fo
AUI'ROR: KaLXabkina, & V. ciences)l Klahkin, SoTe r
DcA
of technical sciences)
TITLE: Radiographic study of oxidation and recrystalltzation processes in the our-1,
71 1
face, zones of nickel-base heat-resistant alloys
SOURCE: Moscow. Aviatsionny y institut. Trudy , no. 158, 1964. Issledovantya
struktury i svoystv zharoprochay kh splavov (Studies on the structure and proper-
,-ties of heat-resistant allovs) _35-42-
TOPIC W;Si.,__
'4l,~yi p-ic 1 alloy. cacidation n
~_s rac
alloy reckystallizatioln _:~~_dlograv Y.--- -surface: oxidation ur ace, recustallizi
0 6
a
1l
ABSTRACT: The purodse of tht sitxl~~Ost ~:Ation: was to determine the stability-of
jourface layers of
gas-turbine blado_=de fromggst allo 617 1
alloy 91437B
.y

7777~7___
0404475k7~'
I.ACCESSION NR:
and recrystallizatio'n, ~Wich 'sho'_we_a:,tha_-'t- --the of oxidation and recr
tion coin(Ades for:_~Rch'4116 th- -' -icesses.start. later at lower temperatures.
Cast alloy was the most stitble. At Ugher tedperi-itures, the differences in
ity of the different alloys become insignificant. Curves are alGo preselited show-
Ing the onset- of ~oxidatiqn,-,as_a__furtc.tAon of annealing time and, using these, the
f
energies of activa-tiouf thd-*recryo~aiiiizatflon,peaceso were calculated from the., r--: -
formula I it where H is the time of onset of recrystallization; T is
R is. the gas constant;
the annea ing em u
om. T
iand QH is the energy of activat an For allay B1437B this was 56 000 ca-l gm-at
The authors conclude that oxidatioWaad rect-
ystalltzation take place simultaneous
t
~Iementb
4 i I I
h# The alloA!~~'
t 'a A 4 -the~7tiicrysta Lied -show-A'att
apparen ly m teF 41Md 211 er ayef;~~ 4ed---E~iiq hii-I
parameters approaching those 6 pure nickel. 'Me~ authors express their gratit4d6l
to x-ray technician_S.P Kulasin.11 Orig. art. has- 3 tables, 2 figures and I
formula.
ASSOCIATION: Moskovakiy avlatsioaayy institut (Moscow aeronautical institute)
SUBMITTED: 00 ENCL: 00 SUB CODEP: M
No REP SOV: 065 OTHER: 000
Card ?
J

S/0181/64/006/005A26i/1266 1;
NRs APW349op
P.;' Svetlov., 1,'L.;,
AUTHURS-i Bokshteyn,, So Z.; Kia~~i~n S. Ti, Hazarova,
Umantsev EO Le
JL
TITLE z erawtlf~ of sapp4ilrw V~isker
SOURCEs Fizika tvardogo tola, v.-6, no* 5j 1964, 126l-i266
TOPIG 'V~ t 'Whisker crystal) crystal growth, sapphire,,- sapphire whisker~.-
ABSTRAGT i. -Whisker crystUs"of-,AlOj:wemgrown by high-temperaWre oxidation of
powdered iietallie Al in anatmosphere'of moist hydrogen. -The reactidirtemperature
vaA__kM1MM400C. e~a special apparatus used for growing these'..
The anthors.describ
arysWs., t~M& comists orthJree essential partat a tubular furnace, a . hydrogen
source,. -md a system for purification and control of hydrogm feed The whisker
fl.crystals ranged from 1 to 30 -~P in diameter and from 3 to 15 M in length@
I j 4"MM Uzals ranged from 30 to 350 it. in diameter,.: aud 0.5 to 3 mm in
111 length. Oospillaries were observed *along the growth axes of some crystals."
1C_
AL

L 5052-65 FI.T(fn)/EWA(d)/"PR/t/~VWP(-t)/EliiP(z),,'FWP(b)/FWA(c) ps-4 IjP(C)
ACCESSION NR: AP5010555-kjv/,M/jv-UR/0129/65!~)OO/004/0036/0038 31
532.72:669.71'72
AUTHOR: Bokshteyn, S. Z_.; Bronfin, H. B.; Ktahkin ?S. Martchev,_V. A..
..O~ .
TITLE: Study of the diffusio. f magnesium in aluminum by means of evaporation
in a vacuum
SOURCE: Metallovedetitya t termicheakaya obrabotka metallov, no, 4, 1965~ -35--3.8
TOPIC TAGS: '"magnesium diffuilon.,~ altkainum alloy, vacuum evaporation, magnesium
containing alloy
77
d ifdofdW-dE_- W
f ' " it died at 44_8
-Vas u
n -ce, SaVles of the Al-Mg alloy Aft6ldontaining
6
6.35% Mg were used. As time elapses, the surface layers of the sample become
depleted of Hg; a concentration gradient is thus created which causes the migra-
tion of magnesium by diffusion from the middle layers to the curface. Subsequ-~ntL
1y, Mg evaporates at the rate at which it is supplied by this diffusion. The
evaporation was determined from the weight loss of the sample, and kinetic curves,
of the specific weight losa under isothermal conditions were plotted for several
temperatures. From these'cUrvea$~the cadficients of diffusion of magnesium in.
1/2
Card

ASSOCTATION: None . -4, 1
v.
SUMITTED - 00 ENCL: 00 SUB CODE: -M, SS
90 REF SOV, 001 OTHER: 003

1q:llMtfl Ago%, i931-F
RtiftRwm ZEZVINM~.-F V-
mm
B(
K EL
I,fLj, ve. TIVvo arid -eat ronl -,j
xid

000/ 2/0129
L 298o0-66 EWT 2/0029
SOURCE CODE1 UR/0000/65/000/000/002
I'ACC NR, AT6016344
S T
Kighkin
,~iqh in T
s.; ZhukhovitskiY4-"
3okshtayn S. Z.; BokahteYn. '3-
AUTHORS:
No i' rov 'Yu-
I -IOe
ayov
ORG: none
f point defects in the.crystal lattice Of
In mAhod for-thO studY 0
TITLE Relaxation
metals
i UkrSSR. Podvizhnostt atomov v kristal3,ichoakoy roshotke (MobilitY Of,
SOURCE: Al Jzd--VO Naukova dumkap 19659 22-29
lattic0). Kievy
atoms in crystal crystal lattice dofect)
crystal lattice,
TOPIC TAGS: metal CrYstalt
3tudy of point defects in metal ,rystal
ABSTRACT: A relaxation method for the 1 icularly suited for the separate
ented. The proposed method is Part mation Qf) and vacancy
lattices is Pres . s of vacancy for A
L the activation anergle
determination of The method is based on the determinatio, .nof
mobility (~, in metal crystal lattices.
the vacancy relaxation time as a function of the tamperaturo
--L 29800-66---
ALL; APL6016344
V. zVb exp (S,.IR) exp Q.11?T
12 4 D,d(
0
D.
6 106exP(Sm1R)exp(-Q /R7)
3 P
-Y. exp S.1k) exp Q
)B
where is the number of vacancy Jumps per second,, Z is the coordination number)
~D is Debye frequency, Sm is entropy of activation for vacancy mobility, 'Ls
distance between sources and sinks df vacancies, .DB is diffusion coefficient of
vacancies, S is lattice constant, and n is the number of vacancy Jumps during
'~T T
The relaxation time is determined by measuring the electrical resistance
of a metal specimen as a function of time and temperature when the s
pecimen is
subjected to rapid heating. The chang Ies in temperature A T A T 31 et C, corre
2)
sponding to changes in resistance A R2 A R , ate for corresponding rates of
3
heating etcp are obtained graphically (see Fig. 1). From these
2J' 3P T
follows as
Tr =LP
us us
bard 2/3

AT6016344
3
Fig. 1. Temperature dependence of the electrical
resistance of metals for different rates of
heating. -1 - lattice with equilibrim vacancies
concentration, small heating rate; 4 A
lattice
without vacancies largo heating rate;
2, 3 - intermediate curves..
T, i, T7
i - --~:,
A ex p (Q,,,IRT~.
and Q. from
The value of Qf is derived from a graph of ln V a The method wAs
R T
tested on aluminum specimens, and a schematic of the experimental installation is
presented. It was found that the relaxation time for Al at the melting point was
0-2
1.9 X 1 sec and Qf = 17 � 4 kcal/mole. A variation of the above method affords
a study of the kinetics for the reestablishment of equilibrium vacancies concentra-
tions. This method is based on the determination of the change in the electrical
resistance 4 R 1 1 - Rol, where Ol is the electrical resistance of an
ideal lattice at T, and is the equilibrium value of the electrical resistance
at Ti
-'~p_ Ap, I "P
Orig. art. has: 7 figures and 4 equations,
SUB CODE: 20 SUBM DATE: O7Dec64
d, 3/3

ljp"c 1, --D/GS/G)-2
ACC NRs AT6012373 SOURCE CODE: UR1000076 5-/*M 82
AUTHORS: Kishkin, S. T.; Polyak, E. V.; Solonina, 0. P.; Molseyev, V. N.; Tarasenkof
iu~rayeva,_T.-7.-
G. N
ORG: none
TITLE- Structuxal JyMerolMation ilf titanija alloys
SOURCE: Soveshchaniye po metallokhimii, metallovedeniyu i primeneniyu titans. i yego
splavoy, 6th. Novyye isaledovaniya titanovykh splavov (New research on titanium
alloys); trudy soveshchaniyas Moscow, Izd-vo Nauka, 1965j 82-86
annealing, phase composition alloy
TOPIC TAGS:A titaniumo titanium alloy, aiectronmicroccopy/ VT3-1 alloy, VT14 alloYt
VT16 alloyt VT15 a~110YP VT10 alloy
ABSTRACT: The #ruotu:ral Awansf9ymations induced by,~tnnealing in ((x + S) alloys of
the types_r3-1_jVVT14,Nnd_VT16 , loy of of ~ii ~01 Ile on-
,Nn d al _IgMk~jid in oc alloy
taining an intermetalloidal strengthening agent, were studied. The study was carried
out by means of electron microscopy. Electron microscope photographs of specimens
annealed at different temperatures are presented. Annealing alloys under different
conditions leads to a phase transformation in the alloys. The optimum phase composi-
tion that possesses m imilm strength and plastici~ w+as found to consist of single o( -
phase regions and highly dispersed heterogeneous OC /6) phase.regione resulting
from the decomposition of the metastable 6-phase. Thermal stability of alloys may be
increased by the addition of aluminum to the alloy, Orig., art, hts# 2 figures.
_'_'[.Card 1/1 -A~4.,w SUB CODE: '11/ SUBM DATE: O2Dec65

L 38909-66 EWT'm)/T/Z'TP'_0/ETI/9WP(k) IJP(c) JD/HW
ACC NR, AP6019769 SOURCE CODE: UR/0370/661000/003/0125/0129
.._(Moscow); Glazunov, S. G. (Moscow); 1~~orev, A. 1, (Mosco
AUTHON, W);
u (Mo
t. (Mosco+
w
Rub in-- u' scow -thilina, E._t!. (Moscow
ORG: none
TITLE: The use of high-temperature thermumechanical treatment-in the manufacture of
extruded BT-151titanium alloy tubes 16 f&
SOURCE: AN SSSR. Izve;stiya. Metally, no. 3, 1966, 125-129
TOPIC TAGS: titanium alloyi alloy tube, tube heat treatment, thermomechanical treat-
ment, high temperature treatment, aluminum containing alloy, chromium containing
alloy/VT15 alloy
ABSTRACT: Vacuum-are melted ingots of VT15 titanium-base ai~loy (2-99-3.05% 4,
10.7-11.1% Cr) were conditioned by machining and extrudedl into bars 187 mm in diam-
eter. The bars were cut into tube billets which were pierced, conditionad and
extruded at 950-1150C Into tubes with an outside diameter of 110 mm and a wall
thickness of 10 mm. Part of the extruded tubes were air cooled and then subjected
to conventional heat treatment (annealing at 800C followed by water quenching);
another part was subjected to high temperature thermomechanical treatment (HTMT),
i.e., were water quenched immediately after-extrusion. Both tube lots were then
I LOW J rob- ujiu: