SCIENTIFIC ABSTRACT BERNSHTEYN, M. L. - BERNSHTEYN, M. L.

• Document Type: CREST
• Collection: Scientific Abstracts
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• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: June 8, 2000
• Sequence Number: 7
• Publication Date: December 31, 1967
• Content Type: SCIENCEAB

SOV/137-57-1-1249
Translation from: Referativnyy zhurnal. Metallurgiya, 1957,
Nr 1, p 163 (USSR)
AUTHOR: Bernshteyn, M. L.
TITLE: On Grain Boundaries in Metal Alloys (0 granitsakh
zeren v metal-
licheskikh splavakh)
PERIODICAL: Tr. Naucho-tekhn. o-va chernoy metallurgii, 1955,
Vol 6, pp 221-
234
ABSTRACT: A critical survey of theories explaining the nature
of grain bound-
aries (GB). A detailed examination was made of the N - T -
Gudtsov
theory, which relates the origin of GB properties that differ
from
the properties of the grains themselves with the distortion
of the
crystalline structure on the GB which develops during the
crystal-
lization of the metal. Various methods were examined for
measur-
ing internal friction (IF), which is the most sensitive to
all changes
of physicochernical properties of GB. A description is given
of a
simplified apparatus for determining the relative variations
of IF.
A detailed examination is made of a hysteresis -meter method
developed by Boulanger (Compte Rendus de s6ance de VAcad6mie
de
Card 1/2 Science, 1951, p 233), the mathematical treatment of
the method is

On Grain Boundaries in Metal Alloys
SOV/137-57-1-1249
discussed, and the results of the apparatus constructed by
that author for the
investigation of the temperature relationship of IF of Al
alloys are adduced.
Ultraviolet microscopy (phase-contrast method) opens the
broadest possibilities
for the study of the GB structure.
A. F
Card 2/2

BZMMnM, M.L.; KISHIUVSKrr, T.B.
Apparatus for ultraviolet microscopy; review of foreign
literature.
Zab.lab.21 no.10:1256-1259 155. (KM 9:1)
I.Obsor zaraboshtykh dwmqkh.
- (microscope)

TE
5408
ULTILAVIDLRT MICRMOPIC MMMATION OF 62-
TrrA?nLfM, MOBIUM, AND CARMN ALLOY STRUCTURE&
V. P. 9]7utLn,M,. L. bemsMaln, and Yu. A. Pavlov. jMoacow
InEt.of8teel). Dok3adyAkad.Nmtkg-'LSJL104.640-8
(1955) Oct. 1. (In RUDBIW
Tht structureB wW propqrtlea cd 1tItRnln=-zdcbiu= alloy
sampleB, melted In vicuum furnarps of grapblie were
stuffled. The zontent of WoMum varied from 1.5 to 8B.4%;
content of c~-bot was vILII* 0.7 to 0.9%. 72ia sx=ples were
temperbd in a vacuum 21 10001C. Ultraviolet micro&mple
studleE delermlmd the pbass cbaratter o1 empt 3nulti-
co=paneml rystems occurring b *ore samplAD. MV.J.)

B]IRNSHTBYNl Mark L'yoviche RAKM , A.G., redaktor;
GCRDON, L.M.o
; YNSHTBYN, Ye,Be, tekhnLoheskiy redaktor
[steals and alloys for use at high temperatures] Stali i
splavy
dlia raboty pri vysokikh tesperaturakh. Moskva, Goo.
nauohn6-
tekhn. izd-vo lit-ry po chernot i tevetnoi metallurgii,
1956. 238 P.
(MIRA 9:10)
(Metals at high temperatures)

PWOEff-ALRU)MY, Georgly Iyanovich; GRUIR, Tully
Alskeandrovich;
RA HTADT, AlekB&ndr Grigorlyevich; IAKHTIN, Yu.N.,
professor,
Aoktor tekhnichookikh nank, "teenzent: I=Sffjrl,
N.L.. dotsent
k&adi&at takhnichookikh nauk. redaktor; PITROVA,
I.17.,lizdatell-
skly rodaktor;.GIADKIKH, N.N.,.tekhnicheakiy re(laktor
[Pbroloal metallurgy; methods of analysis. laboratory
work and
problems] Metallovedenle; netody analiza,
laboratornys raboty i
zadachio Isd. 2-os, perer. Moskva, Goo. izd-vo obor.
promyshl..
1956.427 P- (MILRA 9: 10)
(ftelcal metallurgy)

AVRASIN. Ya.D., kandidat tekhnicheskikh nauk; BM, P.P.,
professor.
doktor takhnicheskikh nauk, qj=, N-j-, kandidat
tekhnicheskikh
nauk; GSNEROZOY, P.A., starshiy nauchnyy sotrtidnik; GLIM,
B.M..
inshenarl DAVIDOVSKAYA, Ye.A., kandidat tekhnichookikh nauk;
YALCHIN,
P.M., inzhener; TARAMIN, N.I., kandidat
fiziko-matematichaskikh nauk;
IYANOV, D.P., kandidat tekhnicheBkikh na* UOROZ, L.I.,
Inzhener;
KOBRIN, N.M., kandidat tekbnicheskikh nauk; KORITSKIY, V.G.,
dots6nt;
XROTKOV, D.V,,, inshener; KUDRYAVTSAV, LV., professor,
doktor takhni-
chSBkikh nauk; XULIKOV, I.Y., kandidat takhniche 'skikh
nauk; LEMOT.
V.A., kandidat tekhnicheskikh nauk; LIKINA, A.F., inzhener-,
NkTvxyzv,
A,Se, kandidat tokhaicheskikh nauk; MILIMLN. B.So, kandidat
tekhniche-
skikh nauk; PAVLUSHKIN, N.M., kandidat tekhnicheskikh nauk;
PTITSYN,
V.I. Inzhener [deceased); RAZOVSKIY, V.S., kandidat
tekhnichGBkikh
nauk: 'RA HTADT, A.G.. kandidat tekhaicheskikh nauk;
RTABCE3NKOV,
A.V., professor, doktor k:h1micheskikh nauk; SIGOLAYEV,
S.Ta., kandi-
dat tekhnicheskikh nauk; SMIRYAGIN, A.P., kandidat
tekhnicheskikh
nauk, SULIKIN, A.G., iuzhen*r; TUTOV, I.Te,, kandidat
takhnicheskikh
nauk, KHRUSHCHOV, M.N., professor, doktor takhnichaskikh
nauk;
TSYPIK, 1.0., kandidat tekhnicheskikh'nauk; SHAROV, M.Ya.,
inshener;
SURMAN, YA.L. dotsent; SHKELIT, B.A., kandidat
tekhnicheskikh nauk;
TUGANOVA, B.A.. kandidat fiziko-matematicheakikh nauk-,
SATIL', N.A..
doktor tekhnicheskikh nauk, redaktor; SOKOLOTA, T.F.,
tekhnicheskiy
redaktor
[Machine builder's reference book) Spravochnik
mashinostroitelia; v
shesti tomakh. izd-vo mashinostroit. lit-ry. Vol.6. (Glav.
red.toma
I.A.Satell. lzd, 2-oe, Ispr. I dop.) 1956. 500 p. (MIRA 9:8)
(Kachtner~--Constructiom)

I I- - .- -1 - - ~ - I - ---- . ..- ~- ., - , r .- - -
~ ~iylll
- ~

F- RN -S "T E Yi4, M - L
ALITGAU=N, O.N., kandidat fisiko-matemisticheskikh nauk; mgmIR
kandidat tokbnieheskikh nauk; BIANIR, X.Too, d0ktor
takhnicheskikh
nauk; BOXSRtXTN, B.Z., iloktor tokhnichookikh nauk;
SOLKHOTITINOU,
Ye*N*, )mndidat tekbnlcheakikh nauk; BORZDTIA. A.M., doktor
takhni-
cheskikh nauk; BUNIN, X.P., doktor tekhnichaskikh nauk;
VINOORAD,
M.I., kandidat tekhniAesktkh nauk-, VOLOVII, B.Ye., doktor
takhnichs-
skikh nauk [deceased); GAMOV, N.I., inzhoner; GILLIR, Tu.A..
doktor
tekhnichookikh nauk; GMUlDi,'S.S., kandidat takhnichaskikh
nauk; I
GOLIDBKBZRG, A.A., kandidat takhoicheskikh nauk; GOTLIB, L.I.,
kandt-
dat takhnichookikh nauk; GRIGOROVICH, V.K., kandidat
tekhnichemkikh
nauk; GULIAYN, B.B.. doktor takhaichaskikh nauk; DOVGALIffSKIT,
Ya.M,
,kandidat tekhnicheskikh nauk; DUDOTTSW, P.A., kandidat
takhniche-
sidkh aauk; KIDIN, I.N.,.doktor takhnicbeskikh nauk; KIPNIS,
S.Xh.,
inzhener; KORITSXIY. V.G.,kandidat takhnichaskikh nauk; IASDA.
AJ.,
doktor takhnicheakikh nauk; LXMIZ, I.M., kandidat tekhnichookikh
nauk; LIVSHITS, L.B...kandidat tekhnichaskikh nauk; LIVOV, M.A.,
kandidat tekhnicheskikh mauk; KALTSHU,K.A.0 kandidat
tekhnichookikh
nauk; MIYUSON, G.A., doktor takhnichookikh nauk; HIMEVICH, A.R.,
kandidat taklmichaskikh nauk; MOROZ, L.S.. doktor tekhnicheskikh
"uk; STANSON, A.Z., Imndidat takhnicheskikh nauk; U"IMOV, A.M.,
inshener; NAKHIMOV, D.M., kandidat takhnichookikh nauk; POGODIN-
ALIKSIM, G.L. doktor tekhnichaskikh nauk; POPOVA, N.M.. kandidat
tekhnichookikh nauk-. POPOV. A.A., kandidat-takhnicheskikh nauk:
RAKH HTAM, A.G.. kandidattekhnichaskikh nauk; XOGILIBUG, I.L.,
imudidat takhnicheakikh nauk;
~ (Continued on next card)

AL'TGAUZRN,,O.1----- (continued) Card 2.
SADOOZIT,, V.D.. doktor takhnichookikh nank; SALTTZOV,
S.A.,
inxhoner; SOBOIJU, N.D., kandidat tekhaicheskikh nauk;
SOLODUHIN,
A.G., kandidat tekhnicheskikh nauk; UMANSKIT, U.S.,
kandidat
tokhnichookikh nauk; 'VfBVSKIT, L.N., kandidat
tekhnicheskikh nauk;
]PRIDNO, Ya.B.. doktor takhnicheskikh nauk; KHIKYSHIN,
F.F..
kandidat tekhnichaskikh nauk.- KEINUSHGHXV. M.N.. doktor
tekhniche-
skikh nauk; CHONASHKIN. V.G., kandidat takhaicheakikh
nauk; SHAPIRO,
M.N.. inshoner; SHEOLINIX. L.M.. kandidat takhniohookikh
nauk;
SHRAYBER. D.S., kandidat tekhnichaskikh nauk; SHOWOV,
N.P., doktor
takhnicheskikh nauk; GMY-PSOV . N.T.. akademik.
redaktor; GORODIN.A.M.
redsktor izdatelletya; VAYNS11TON, Te.B., takhnicheakiy
redaktor
[Physical metallurgy and the heat treatment of steel and
iron; a
reference book] Metallovedente i termichesWa lobrabotim
stali i
chuguna; spravochnike Pod red, N.T.Pudtoova,
M.L.Bernebtsinag A.G.
lakhahtadta. Xoskva,.Gon. nauchno-takhn. izd-vo lit-r7
po chernoi i
tevetnoi metallurgii. 1956. 1204 p. (KIRA 9:9)
I., Chlen -korrespondent Akadeall nauk USU (for Bunin)
(Steel-Eeat tteatment) (Iron--Heat treatment)
(Physical metallurgy)

~. - , , _ e
lx-
p~,-
1- "Li.4

E~ N
GMTSOVI N.T., akadeollk-, 4-~4~dat, tokhnicbeskikh nauk',
*Tool GUOISM N.A. Geller. Bovlgvod by N.T. Gpd$sov,
M.L. Bernahtsin. Notalleved.,-A Or. mt. no.9158-60
S 156. (MMA 9%11)
(Tool stool)
Weller, IU~A.)

R;A MIK

13]MSHTBYN.. K,U,- referent-.. ... - . . I
- I ,
Color aderoAotagraphs of Iron &1loys. Uv. lab. 23
no.3:338 157.
(Iron &lloy9--1bt&llqgr&pby) (XIIIA 10W
(Photoularogr&pby)

ATITHORS: Berniteyn, M. L., Candidate of Technical Sciences
32-10-16/32
11iii Ner, i. Ye.p Professor~ Doctor of Technical Sciences
Lozinskiy, 1J. G., Doctor of Technical Sciences
TITLE: Achievements-and Tendencies in the Development of
Soviet
MetaUogrq* (Dostizhen--ya i tendentaii v razvitii sovet8koy
metal.lografti
PERIODICAL: Zavodskaya Laboratoriya, 1957, Vol 22,~, Nr 10,
PP 1202-1211 (U3SR)
ABSTRACT: In the introduction the history of the
development if micro-
and macroscopic research work carried out in the world
(since the'end of the 19th century) and in the USSR (since
the October revolution) is described. The report is divided
into 3 chapters entitled;
1.) Liclib nicroscopy. As the most notable the viork
carried out
in this field by D. N. Rozhdestvonskiy, S. I. Vavilov,
V. P. Lennik, and A. A. Lebedev is described. The optical
industry of the USSR is at present producinE the followinc-
apparatus (which are here described as being up-to-date):
microscopes "MMM-811, 1114MM-611 and '%MM-S, which are
remarkable, besides their very uniform illumination, also
Card 1/4 by an add.:tional lateral illumination and are
destined for

Achievements and Tendencies in the Development of Soviet
32-lo-i6/32
Metanography
enlareements of up to the three-fold. For the increase of
the contraut effect (upcn which special stress is laid here)
an Rdditional device is provided for the microscope
"MOL-811 consiatine of: a metal ipirror condenser with
parabolic reflection, it rinL-shaped diaphragm, and a
shiftable auxiliary line. For thia purpoot) a dark field
Is used. Furthernore-, the uge of "conical" and "polarized"
liC,ht in the microscope is mentioned, but the implei.-ients
necessary far this purpose are not described. As one of the
111tist achievements of optical technical eneineerinj,,11 the
method of phase contrast is mentioned,which is based upon
a specially constructed additional device "Kq-3" for the
micro-scope 11L:M M-811. Another additional device, called
11MV, wakes it posnible to take photoi:raphs in the microscope
by means of an ordinary camera. Furthernore, the "hiCh
pressure mercury lij:ht source" is described here as well as
shortrave ultraviolet rays in the microscope in connection with
the chanCe of color. The respective apparatus is not described.
Further, the newly constructed microscope "MM L-14" with
remote control for radioactive subs'ances and a television
Card 2/4 microscope, which radiates a picture from a microscope
on to

1chievements and Tendencies in the Developm6nt of Soviet
32-10-16/32
Meta,Uogmyhy
a Screen, are mentioned. The make is not mentioned.
2.) High-Temperature IletalloFraphy. Works by I. A. Oding,
and M. G. Lozinskiy of the Institute for Machine Science of
the AN USSR are referred to. Research methods are divided
into two groups: 1.) Methods for the investiCation of the
microstructure of heated metala and alloys, and 2.) methods
for the investigation of the properties of metals under
the influence of different temperatures. In Ceneral heating
in a vacuum (in rarefied air) is dealt with, because, if these
conditions prevail, the formation of crusts and films can be
avoided. As a device suited for this purpose the 11 HMAW -BM"
is mentioned, which makes it possible to carry out research
riork at temperatures of up to 11000C at vacuum tensions of up
to 60 kg/mm2 and to measure deformations. 3.) Measuring
metallography (here described as utilization metallurgy). It
consists in the measuring and Judging of intercrystal and
other structural intermediate distances, austenite trans-
formations, structural shilfting and other structural changes
occurrine in alloys when they are thermally or mechanically
Card 3/4 etc. treated. The most important works in this fields
are by

Achi'4,inents and Tendencies in the Development of Soviet
32-10-16/32
S. A. Saltykov, I. L. Mirkin, A. A. GlaColev and the "very
latest" are by L. S. Morozov, N. N. Sirota, S. Z. Boksteyn
and M. H. Steinberg (this is an extract from the total list).
There are 5 references, all of which are Slavic.
AVAILABLE: Library of Congress
1. Science-USSR-Progreas 2. Microscopy
Card 4/4

SOV/137-58-9-19936
Translation from: Referativnyy zhurnal, Metallurgiya, 1958,
Nr 9, p 263 (USSR)
AUTHORS: Bernshteyn, M.L., Grinberg, M.L.
TITLE: ThM"Muen"*677o"~' ~R~ciystallization Texture Upon
the Mechanical
Properties of Metals (Vliyaniye tekstury rekristallizatsii
r,~a
mekhanicheskiye svoystva metallov)
PERIODICAL: Metallovedeniye i term. obrabotka. Moscow,
Metallurgiz-
dat, 1958, pp 65-78
ABSTRACT: A study is made of the influence of plastic
deformation and
texture t pe upon the strengths of Armco Fe under various
.1y
types of loading. It is established that the texture
resulting
from rolling increases Ts to a greater degree (from 20.6
to 90.5 kg/mmz in tension and from 13.65 to 42.0 kg/mmz in
torque) than does the texture resulting from drawing (up to
72.6 kg/mm?- in tension and 31.Z kg/mmZ in torque). The
different effect upon increase in a-8of rolled and drawn
spec-
imens is the consequence of differences in the texture of
the Fe.
In rolling, the metal undergoes work-hardening considerably
more intensively in the vicinity of the (100) plane than in
Card 1/2 drawing, even if the, degree of reduction is
identical. In

SOV/ 137-58-9-19936
. The Influence of Recrystallization Texture (cont.)
tensile testing, tbe a-S of dravift and rolled specimens is
higher than in
torque testing. Bibliography: 16 references.
F. U.
1. Metals--Vachanical properties 2. Metals-Crystallization
3. Crystal
structure-lietallurgical effects
Card 2/Z

80189

SOV/123-59-23-97020
Translation Prom- ReferatIvu Nr 8 U
>,y zhurnal, MashinostroyanlYe, 1959, 23, p 11 SSR)

AUTHOR:
j3ornshteyn, M.L.
TME:
The Effect of Cold Hardening on the Structure
and Properties of Heat-

Resist S r e oys
PERIODICAL:
Tr. Sektsii
metalloved. i term. obrabotki metallov. Tsentr. pravl. Nauchno,
.
.
tekhn. o-va mashinostroit. prom-sti, 1958, Nr 1, pp 230 - 265
ABSTRACT:
The theoretical conception of the/ hardening effect of
cold-hardening was

examined with specimens of �~Illgrade steel.of the
following composition.

(in %): C - 0.11; Cr - 17; Ni - 24; Mo-- 6
64; N - 0.12; with
'
l
4

specimens of Ni-alloy contoning 0.07
5% C, 20_
Cr,
o4% Ce, 2.6% Ti,

0.56% A10 and of the ME6_01'alloy (15% Cr, 62.5%
Ni, 21.2% Fe and 6.19% C~

The specimens of gQqOgrade steel were
subjected to cold hardening by

stretching with 20%-elongation and
subsequent aging at 600 - 9000C with

holding in-the course of from I
- 100 hours. The second lot of specimens

underweUt.aging immediately
after hardening. The specimens of the NI-alloy

(E1437) were,
-cold,-hardened by rolling. and -drawing with -.a rednation of
5,54'

C -1 1/2
Cold deformation was effected-after hardening at-various
coolW-,
and 75%,

80189
SOVV,123-59-23-97020
The Effect of Cold Hai~dening on the, Structurls., and- FropartAe-s
~ of-Heat-Resisting St,641
Grades and Alloys
rates, followed by aging vit-500 - 8009C with4 holding in- the
course of from 5 - 5, 000 min.
The specimens of KhN60 allok underwent rolling and drawing with 50%
reduction; Thecold-
hardened specimens were subjected to- various forms of, mechani:cal
testing-, Also the- speci fl, o
electric resistance,and "hot"-hardness,.measured In the vaouum.:
were deteftined; It-was
found that the distribution and size of particles of the hardening
phase are important
factors, specifying the heat resistance of the steel. The
distribution of the phases being
formed during the aging process, affects the toughness and the
ductile characteristics of
the steel. The particle size determines the hardness and strength
characteristics during
short-term tests. The size and distribution of particles of the
hardening phase affect
the characteristics of long-time and fatigue strength. 15 figures.
S.E.D.
V
Card 2/2

~VTHORS: Bernsht Knizhnik, G. S. SOV/163-,58-4-37/47
.C
JTITLE% Influence of Cold Hardening on the Physical Properties of
Technically Pure iron (VI'Lyaniye naklepa na fizicheskiye
avoystva tekhnicheaki chistogo zheleza)
PERIODICAL: Nauohrqye doklady vysshey shkoly. Metallurgiya,
1958, Nr 4,
pp 214-219 (USSR)
ABSTRACT: This investigation concerned the influence of cold
plastic
deformation at different states of tension (rolling and drawing)
on the charZe of physical prope=tieB of technically pure iron
with the follow!ng composition: 0.05% Cp 0.12% Mn, 0-17% Sit
0.001% St 0.00'1% P, 0,00028% A!20 30 Magnetic permeability of
the
material in dependence o.-. the field intensity of the
magnetizing
field N(H) was measured en an anisometer of the system of
W. S. Akulov particularly prepared for these purposes. The
fnllowing facts were ascertained by the investigation:
1) At great deformations causing a formation of texture tho
magnetic permeability is reduced. Magnetic permeability of the
rolled samples is lower than that of the drawn samples.
Card 1/2 2) Coeraive force of the rolled samples is greater than
that of

Influence of Cold Hardening on the Physical SOV/163-58-4-37/47
Properties of Technically Pure Iron
drawn samples. 3) Electric resistance of the rolled samples is
higher than that of drawn samples. A continuous increase of the
e,le-_tr-_*u resistance is, however, observed with an increase in
the degree of deformation. 4) The blurring of the diffraction
!ines on, X-ray diagrams taken of samples deformed by rolling and
dr&wing is stronger in drawing than in rolling (at any degree of
da-formaticn). This can be explained by the formation of great
tans-'%,.~ns of the second type and a higher refinement of the
blooks in drawing than in rolling. The tensions of the second
type, blurring cf.the X-ray lines. (in the original,
distort-ions and.tensions of the second and third types are
mixe -1 ul, ) 5) It is assumed, that the changes
of properties ascertained are determined by the fact that the
tensions of the third type are greater in rolling than in
drawing. There are 4 figures and 1 Soviet reference.
ASSOCIATION. Moskovskiy Inatit-at stal-I (Mescow Steel Institute)
SUBMITTED: January "1, 1958
Card 2~2

69402
BOV/337-59-4-86%
Translation from;
Referativnyy zhurnal, Met&Uurgjya, 1959, Nr 4, p 193 (UBSR)
AUTNOIRS: Gu0sov, N.T., Trubetskova, R.L., I. ~,Mshteyn,, M.L.
-- -- -4
The 0V1
TITLE: Effect of Small Admixtures of Boron,'Caloium Niobium,
Zirconium"
and Cerium on Me,Struoture and Priip~rtlei -ofHIgh:Vi-ake1
Heat-Resistant
Allo a
=~Lio I .~1;1
PERIODICAM Sb. Mosk. stmal. 1958. Vol 38, pp 495 - 516
ABSTRAM The authors Investigated the effect of small admixtures
of B (0.005%),
Ca (0.3$), Nb (0.5%). Zr (0.2%) and Ce (0,01%) on the structure
and.
properties of 436KWMO~Jtype alloy. To Investigate the effect of
the
crystal izatiqu rate of the metal, the ingots were cast into
molds cooled
with water, In air and in sand. Aging processes were investigated
an
forged specimens at 700 - 8500C after preliminary quench
hardening at
1,2000C. It was stated that Increased crystallization rate of the
alloy,
that, did not oontain.admixtures, reduced considerably the extent
of the
zone ef columnar crystals and led to a general refinement of
crystallites.
The same result is obtained by means of small admixtures of
elements under
Card 1/2 any conditions of crystallization. The greatest effect
on changes in the

69402
SOV/137-59-4-8686
The Effect of Small Admixtures of Boron, Calcium,, Nioblum, Zirconium and
Cerium on
the Structure and Properties of High-Nickel Heat-Realstant Alloys
macrostructure is exerted by Ce, followed by Zr, B, Nb and Ca. Aging entails
in-
creased hardness of all alloys. Alloys with small admixtures showed stronger
solidification in aging, than an initial alloy without admixtures. Alloys
with ad-
mixture of Nb, B and Zr showed the highest hardness at all investigated
temperatures
and times of aging. Raised proneness to aging and lower proneness to
coaguletion of
particles of the strengthening phase in the alloy was confirmed by data
obtained by
measurements of electric resistance in continuous heating of alloys up to
1,2000C.
Creeping tests of the alloys showed that small admixtures furthered increased
heat
resistance, obviously on account of their refining effect on the grain
boundaries of
the alloys.
V.M.
Card 2/2

PHASE I BOOK EXPLOITATION SOW 5555
Bernshteyn, M. L. , Docent, Candidate of Technical
Sciences.
Kurs lektBiy po metallovedeniyu, oborudovaniyu I
tekhnologii termicheskoy
obrabotki metallov; metallovedeniye zharoprochnykh splavov
(Lectures on
Physical Metallurgy, Equipment, and the Process of Metal
Heat Treatment;
the Physical Metallurgy of Heat-Rebistant Alloys) Moscow,
1959. 49 p. 300
copies printed.
Sponsoring Agency:. Moskovskiy institut stall im. 1. V..
Stalina. Kafedra
metallovedeniya I termicheskoy obrabotki.
No contributors mentioned.
PURPOSE: This booklet is intended for students at
metallurgical school's and
for general readers interested In Soviet progress in
physical metallurgy.
Card 1/2

Lectures on the Physical Metallurgy (Cont.) SOV15555
COVERAGE: Principles of the physical metallurgy of
heat-re.4istant steels and
alloys are reviewed along with the development of testing and
equipment oper-
ating under high pressures and at a high temperature. Efforts
made to in-
crease the heat resistance of steels and alloys and to improve
their creep
resistance and endurance are outlined, and the gradual progress
made in this
direction during the prewar and postwar years is described.
Characteristics
of steel and alloys used in the Soviet Union at various times
are given and
trends in the development of new heat-resistant alloys are
indicated. Acade-
mician A. A. Bochvar is mentioned as an outstanding Soviet
scientist who has
contributed greatly to the progress made in the field of
physical metallurgy.
There are no references.
TABLE OF CONTENTS-
AVAILABLE~ Library of Congress (TA490. B38 1959)
VKIwrc/bc
Card 2/2 10-31-61

9(6) SOV/32-25-2-31/76
AWTHORS: Bernshten, M. L., Paisov, A. I.
TITLE: Electron Microfractography (Elektronnaya
mikrofraktografiya)
Survey of Foreign Publications (Obzor zarubezhnoy literatury~
PERIODICAL: Zavodskaya Laboratoriya, 1959, V41 25, Hr 2,
pp !86 - 189 (USSR)
ABSTRACT: Compared with ordiriary microscopes electron
microscopes have
a much greater focus depth and thus permit promisirg develop-
ments of electron microfractography of metal fractures and
crystal textures. The-pioneering work in this field was done
by C. Crussard and others (Refs 1-6). Coal replicas are
applied by means of two coal atomizers (Ref 3). The replicas
can be removed chemically (Refs 8,9) or electrolytically
(Ref 4). The article contains explanations of fractures re-
sulting from slipping, and pertinent microphotographs
(Figs 1-3). A microphotograph of a fracture with "cavities"
(Fig 4) which is characteristic of "tough destructions" is
also discussed. A fracture along ihe* gliding surface (Figs
5,6)
is discussed with reference to the studies made by Collette,
Card 1/2 Crussard (Ref 4) and others (Refs In the explication'

Electron Microfractography. Survey of Foreign
SOV/32-25-2-31/78
Publications
of intercrystalline destructions observations made by
Brammar, Honeycombs and Ward (Ref 9) Crussard et al
(Refs 3,6), Be'nard and Moreau (Refs ;1,12) are mentioned.
There are 8 figures and 14 references.
Card 2/2

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0 1 1

BERNSHTM, M.L., kand.teklin.nauki POLYANSKAYA., L.V., inzh.
---------------
Effect of peening on the structure and properties of the
VT2
titanium, alloy. Trudy Siknetallovedi term.obr.met.NTO
nash.prom.
no,2:1&-24 160. (MIU 3.4;4)
(Titanium a3loya-Meta.Uograpby)
NRYOns'- conection*-Of- art1*2Isa.U.InU .. inde-d
for-ustanurgist.s.
an neeres--go-sollontulo research workers.
F11-21 " Mir N I,
"MCIUS A HOIW~dasorl - .'
MMM
Or "DOMIMb 141004"tOd bW mw"M of M. (301~ntlfla Technical
~'-*Qexetv) OrIbe, 6"Ung-OulIdIng Intmtry U the field of
beat treatbant of steel, Rest
Ot -
alloys.-: No personalities am
IMUOnGdo Mat Of- SrUGIOM are a&*oNPwIs4 by 3oviet and non-
SOVIOt references and contals conclualons'. dram from
inv*aU-
nations.

82719
S/133/60/000/004/008/0110
I-ro A054/AO26
AUTHORSt Bernshteyn, M.L.; Svistunova, Z~V., Candidates~of
Technical
TITLE: The Effect of Cold Hardening on the Structure and
the Proper-
ties of the W437 (~I437) grade Heat-Resisting Alloy,~/
%16
PERIODICALs Stall, 1960, No. 4, pp. 358 - 362
TEXTs The structural changes of the B1437 type alloy during
cold
treatment, aging and the mechanism of strengthening are
discussed. A nick-
el-chrome alloy, E1437, with the following composition was
testedi C 0.075%f
Mn 0.22%; Si 0.47%; 8 0.0047%; P 0.009%; Or 20-52%; Ce
0-00i Ti
2.62%; Al 0.56%; Cu 0.02%; Pe 0.001%; Ni res. The alloy was
rolled
and drawn to harden it, quenching was started at 1,0800C,
cooling was car-
ried out by water, air and in the furnace (between 1,080 -
700OCs 1250C/h
and up to 500OCs 40 - 5000/h). After quenching and
deformation the samples
vere repeatedly heated up to 50000, 60000, 7000C and 8000C
for holding times
up to 50,000 min, with compressions of 5%, 25%, 50- and
75~o. The effect of
various factors on the hardness and the electrical
resistance of the alloy
nArd 1/4

827:19
S/133/60/000/004/008/010
A054/AO26
The Effect of Cold Hardening on the Structure and the
Properties of the
914437 (E1437) Grade Heat-Resisting Alloy
were analyzed in detail. It was found that the hardness of the
alloy grows
in each case of deformation in proportion to the degree of
hardening, on
account of the desintegration of the blocksp the increase in
secondary dis-
tortion and the decomposition of the solid solution. The
changes in hard-
ness and electrical resistance observed at 5000C indicate that
the decompo-
sition of the solid solution starts already at this
temperature. The in-
crease in electric resistance is more pronounced in the samples
deformed
than in those not deformed due to the formation of atomic
segregations in
the solid solution. This increase depends on the rate of
previous deforma-
tion, its accumulated energy contributing to the development of
heterogene-,
ity in the solid solution upon repeated heating. The electrical
resistance
is stabilized after a holding time of 5,000 min indicating two
simultaneous
processesi the decrease-In electric resistance during the
decomposition of
the solid solution will be compensated by an increase upon the
formation of
heterogeneity, similarly to the phenomenon observed in
"natural" aging. At
6000C the formation of heterogeneity in the solid solution and
aging is mare
Card 2/4

82719
B/133/60/000/004/008/010
A054/AO26
The Effect of Cold Hardening on the Structure and. the Properties
of the
9W437 (E1437) Grade Heat-Resisting Alloy
intensive than at 50000. At a compression of 75% a decrease in
hardness
could be observed by a partial reorystallisation during a long
heating in-
terval. At 7000C hardness and electric resistance display a change
which
is characteristic of dispersion hardening. In samples considerably
de-
formed high and stable values for hardness were observed. At a
compression
of 50% the hardness does not decrease, not even for a holding time
of 509000
min. According to X-ray analyses, the secondary distortion
partially de-
creases when increasing the heating time at 700OC- When heating for
50,000
ming these distortions, as well as the indices for hardness, are
identidal
for samples treated by rolling and drawing. Electron-microscopical
tests
ptoved that the high degree of hardness in samples compressed to
50% after
a long aging is due to the maintenance of a highly dispersed
condition of
the second phase. The drop in hardness after 50,000 min is not only
due
to the coagulation of the second phase, but also to the beginning
of re-
crystallization which is mainly remarkable in samples compressed to
75%. At
8000C decumposition, coagulation of the aecond phase,and the
recrystalliza-
Card 3/4

8273.9
S/133/60/000/004/008/010
A054/AO/26
The Effect'of Cold Hardening on the Structure and the
Properties of the
N437 (E1437) Grade Heat-Resisting Alloy
tion are still more pronounced. The decrease in hardness
due to coagula-
tion and recrystallization sets in the earlier, the greater
the compression.
The X-ray analysis of electrolytical deposits discovered in
samples compTes-
sed to 50% and 75%, after aging for 30,000 min at 8000C,
showed that hardei-
ing with the accumulation of surplus energy promotes the
transformation of
the cubic face-centered, metastable VI-phase into a more
stable-i7-phase
(NijTi type) with hexagonal lattice. It can be concluded
that the recrys-
tal ization of the cold-hardened E1437 alloy results at a
long and repeated
treatment at 7000C in the decrease of heat-resistance at
this temperature.
When heat treatment is carried out at 600 - 6500C, where
the strengthening
effects of tempering can still be maintained, the
heat-resistance of the
metal increased after the thermo-mechanical treatment.
There are 7 figures,,
1 table and 9 referencest 8 Soviet and 1 German.
Card 4/4

69385
S/129/60/000/06/002/022
o So E073/E535
AUTHORS: Bernshteyn, M.L., Candidate of Technical Sciences and
-CVz Zhl_-~Chzhan, Engineer
TITLE: Influence of Work Hardening an the Fine Structure of
Heat Resistant Austenitic Steelsd
PERIODICAL: Metallovedeniye i termicheskaya obrabotka metallov,
1960, Nr 6, PP 7-9 + 1 plate (USSR)
ABSTRACT: Rods of 20 mm diameter from commercial melts of the
following chemical compositions were investigated:
14E169 - 0.48% C, .13.92% Cr, 14.34% Ni, 0.3% Mo, 2.54% w;
A139 - 0.08% C, 15-91% Cr, 25.o4% Ni, 6.4% mo, 0.15% N
2
The steel R1395 was quenched in water after heating for
40 mins at 11800C. Following that, the specimens were
machined, cold rolled and drawn with reductions of
25, 50 and 75% and then aged. Then, the specimens were
subjected to X-ray diffraction and microscopic studies
measuring also the hardness and the electric resistance.
The size of the blocks and of the typpq II distortions
were determined by means of a 1~~- Q~Ilionlzation device
Card 1/4 using iron X-radiation. The widths of the (111) line and

69385
S/129/6o/ooo/o6/002/022
E073/E535
Influence of Work Hardening on the Fine Structure of Heat
Resistant
Austenitic Steels
of the (311) line were determined and from the (311) line
the lattice parameters were determined. In the hardened
state the steels E1395 and E169 have a single phase solid
solution structure with hardness values of HB 186 and 239.
The high hardness of work hardened specimens (plot, Fig 1)
is due to the formation of fine submicroscopic structural
nonuniformities and decomposition of the saturated solid
solution. The rejected disperse phases are distributed
uniformly throughout the body of the grain. X-ray
diffraction studies have shown that, irrespective of the
type of deformation, intensive fragmentation of the
blocks will occur with increasing reductions resulting
from plastic deformation in the cold state (Tables I and
2). The here.given as well as other results show that
the changes in the type Il distortions of various alloys
differ. It Is probable that changes in the type II
Card 2/4 distortions are linked with the formation and
annihilation

69385
S/129/6o/ooo/o6/002/022
E073/E535
Influence of Work Hardening on the Fine Structure of Heat
Resistant
Austenitic Steels
of differing dislocations at the block b daries in
the case of large reIduc tions. "Mal y
For a::Zing, lo S the
process of hardening depends on the rejection and the
character of the distribution of hardening phases
during plastic cold working and during the subsequent
heating. Metallographic Investigations indicate that
work hardening changes greatly the structure of the
alloys; numerous sliplines and twins formed in the
Investigated steels as a result of cold rolling or drawing
which were distributed along the entire grain (Figs 2 and
3). Plastic deformation in the cold state leads to an
increase in the electric resistance as a result of
distortions in the crystal lattice and an increase in
the micro-stresses, whilst decomposition of the solid
solution by the plastic deformation brings about a drop
in the electric resistance (Table 3); the small change in
the electric resistance of specimens reduced by 25% is
Card 3/4 obviously due to the compensation of these two
factors.
L0<

69385
S/129/60/000/06/oo2/022
2073/E535
Influence of '.Vz';A1':kn''rden*iig on the Fine Structure of Heat
Resistant
Austenitic Steels
If the reduction in increased,to 75%, the specific
electric resistance decreases appreciably which shows
the predominance of the influence of decomposition of,
the solid solution. Measurement of the lattice parameter
after cold rolling showed that this parameter decreased
intensively with increasing reduction (Fig 4); thiscan
be considered as a direct proof of the decomposition of
the saturated solid solution as a result of work hardening.
There are 4 figures, 3 tables and 1 Soviet reference.
ASSOCIATION: Institut stali (Pteel Institute)
Card 4/4

81879
8/129/60/000/08/006/009
B073/3135
AUTHORS; Bernshl2mil-K.6 (Candidate of Technical Sciences)
In-d Kovaleva, A.D. (Engineer)
TITLE: Changes in the Structure of the Cold Worked Steels
lKhl8N9T.andAa21T during Heating
PER.-IODICALs Metalloveden!"Ye I termicheskaya obrabotka
metallovt
19609 No 81 pp 25-30 (+ I plate)
ABSTRACT: The steels referred to are used extensively drip
to
their resistance to the effect of acids, scale
resistance'land also
heat resistance. Daring the process of manufacture of cold
rolled
or drawn tubes made of austenitic and ferritic steels,
difficulties
arise which are due to changes In the structure and
properties of
the metal and which are not always.fully explained. For
elucidating the nature of some of these changes,
investigations
were carried out which are described in this paper. The
chemical
compositions.of the investigated steels were as follows:
Steel Kh25Tt 0.15% C; 0.9% Si; 0.77% Mn; 26.7% Cr; 0.4% Ni;
A 17'Aff Ti
X
Ts 0.11% C; 0.62% Si;
0.17% Mn; 17% Cr; 8.7% Ni;
,

81879
S/129/60/000/08/006/009
B073/9135
Changes in the Structure of Cold Worked Steels lKhl8N9T and
Kh25T during Heating
Prior to cold rolling and cold drawing the blanks were pierced
and rolled in hot rolling stands and subjected to preliminary
tests. After hot rolling the tubes were quenched in water from
1100 and 950 OC respectively. Following that, the tubes were
cold
rolled or cold drawn with maximum degrees of deformation so
as to
obtain clearly pronounced textures. The reductions were 75%
for
the steel lKhl8N9T and 95% for the steel Kh25T. From the tubes
20 x 20 mm specimens were-out which were heated to 4oo, 50o,
6oo,
700 and 800 OC and held at each temperature for durations of
11
5) 25, 50 and 100 hours. The structural transformations were
studied by hardness measurements, microstructure study with an
optical microscope, static metallography and X-ray structural
analysis. The results of the changes in hardness and
stretching
of the grains in cold drawn and cold rolled tubes from the two
steels are entered in Figs 1 and 2, and 3 and 4, respectively.
The results show that quenched and cold worked austenite of
the
steel lKhl8N9T is more inclined to develop phase
transformations
leading to an increase in hardness than annealed and cold
deformed
austenIte which is characterised by a greater stability.
^ - -.2 'D /L

81879
S/129/60/000/08/006/009
3073/3135
Changes in the Structure of Cold Worked Steels lKhl8N9T and
Kh25T during Heating
Although the general relations remain the same, comparison
of the
graphs in Figs 39 1+ with those in Figs 11 2, lead to the
conclusion that in the steel Kh25T the transformations are
considerably slower than in the steel lKhlBNgT. It is
possible
that this is due not only to the differing nature of the
forming
phases~ but also to a generally lower level of type II
distortions
in the ferritic steel than in the more strongly
work-hardened
austenitic steel. The experimentally established martensitic
transformation in the steel lKhl8N9T and the formation of a
a phase in the steel Kh25T during repeated heating of cold
worked
specimens lead to a further conclusion relating to the
influence
of the accumulated deformation energy on the distribution
of the
individual elements in the solid solution. The determined
transformations in both these steels could not occur in the
equilibrium state. Such occurrence is made possible in the
temperature range 400-600 OC by a redistribution of the
elements
which leads to a lowering of the solid solution and
formation of
Card 3/1+-

81879
8/129/60/000/08/006/009
3073/E135
Changes in the Structure of Cold Worked Steals lKhl8N9T and
Kh25T during Heating
islands which are poor in nickel. Apparently such lowering
leads In many cases to the formation of thermodynamically more
stable alloys,
There are 5 figures.
ASSOCIATIONO. Moskovskiy institut stali
(Moscow Steel Institute)-
Card 4/4

83.996
J1,bq 4045 11454 S/129/6o/000/Olo/oo5/oo9
9193/3483
AUTHORs -BernshteXg, M.L.,_ Candidate of Technical Sciences
TITLE: ThermomMechanical-Magnetic Treatmentoof Metals and
Alloys
PERIODICALt Metallovedeniye i termicheskaya obrabotka metallov,
1960, No.10, PP-31-36
TEXT: The object of the investigation, described in the present
papers was to compare the mechanical propertiesg(yield point,
U.T.S., true tensile strength, elongation, reduction of area,
impact Itrength) of tee tnical grade iron and steels 20,1V45,1q
V7 (U7)\Iand 912 (V12),~ heat-treated in the normal wWy_
(iju-enched
and fe-mpered where applicable) or subjected to so-called thermo-
mechanical-magnetic treatment. The treatment consisted of the
following% (a) heating the specimens to the austenitic range
(800 to 9500C, depending on the composition of the material) and
holding at that temperature for 20 mini (b) subjecting the
specimens maintained within the austenitic range to hot plastic
deformation (by tension) in such a manner as to prevent
recrystallization of the material; (c) water- or oil-quenching
the specimens placed in a magnetic field. The beneficial effect
Card 1/2
of
of

83996
S/129/6o/ooo/010/005/009
E193/E483
Thermo-Mechanical-Magnetic Treatment of Metals and Alloys
this treatment varied, depending on the composition of steel and
degree of plastic deformation, but the improvement in the
properties studied was noticeable in every case and the material
treated in this manner was free from the tendency to temper-
brittleness. The improvement in the mechanical proper-'lies
brought
about by the thermo-mechanical-magnetic treatment is attributed to
the following factors: (a) formation of preferred orientation due
to plastic deformationj I(b) fragmentation of blocks due to
magnetostriction; (c) refining of the microstructure due to
favourable arrangement of the martensite crystals which tend to
orientate themselves with their long axes parallel to the
direction
of magnetization; (d) the arrangement of martensitic crystals,
imposed by the magnetic domains' structure, minimizing the effect
of
the grain boundaries in the original austenite on the properties
of
martensite, particularly its proneness to temper brittleness.
There are 4 figures and 8 Soviet references.
ASSOCIATIONs Moskovskiy institut.stali (Moscow Steel institute)
Card 2/2.

20256
OCI a" S/148/60/000/011/013/015
A161/M30
AUTHORSt Bernshteyn M. L.j Tung Su-!,.uei, Svistunovt Z.V.
TITLEs The effect of workhardening on the fine structure of the
E1437
alloy
PERIODICALr Izvestiya vysahikh uchebnykh zavedeniy. Chernaya
metallurgiyas
no.11, 1960, 125 - 132
TEXT: The Moscow Steel Institute has studied the effect of work-
hardening on the heat-resistant J%437 (E1437) alloy. The
composition of
the specimen's wast N) 0.05 C~ 0.04 Mn; C.46 Si; 20.8 Cr; 2-4 Ti;
0.8 Ali
0-004 3; 0-007 P; 0.05 Ce; 0-05 Fe; 0.04 Ou.; the content of
harmful impuri-
ties (I?b, 5b, As, Bi and other) was not beyond the amount
permissible. Work-
hardening was applied to blanks out from rolled 35 mm diameter
rods,
quenched from 10800C (and soaked for 8 hours) and cooled in airy
then aged
at 7000C for 5~9 500, 5000 and 50,000 minutes. One part of the
blanks was
cold rolled with 25 - 50 % reductionjone part cold drawn with the
same re-
duction, and one part left unworkhardened. The structure was
studied with
Card 1/6

20256

S/148/60/000/011/013/015
The effect of workhardening on the
.
. .
A161/AO30
an optic and an electronic microscop
e, and
with an
X-ray camera. The ar-
ticle includes photo micrographs and
graphs
showing the measured variations
of hardness and electric
resistance,
and of
the structure block dimensions
and
mioxostresses. It was stated th
at the
workhardened metal was not
homo-
geneous. [Abstractor's notet Photomi
crograp
ha in the
abstract are cuts
from the original in the article.]
The num
erical
data obtained are the
followingi

Hardness
Blocks
size Distortions of
The working RV
1) 10-81
CM2 2nd order 10-3
Quenching only ........
150
1500
0.88
Quenching + rolling 267
670
1-40
(with 25% reduction)
....

Quenching + rolling

(with 50% reduction) .... 340
220
1.64
Quenching + drawing

with 50% reduction) .... 380
6

370

2.18
ard 276

20256
S11481601000101119131015
The effect of workhardenin- on the .... A16l/AO30
The structure seen under the electronic microscope was
hetero-eneou .a
(Figure 6) even without heat application after coldworking.
The variations
of electric resistanoe indicated very intensive further
aging, though the
dimens ons of the second phase remained very disperse and
mu8h smaller
(-300 i) than in specimens left-without workhardening (-700
A)- This phe-
nomenon is apparently connected with the refining of the
blocks and more
uniform distribution of the second phase particles that are
located not on
the grain boundaries only but also on the lines of shearing
and twinning.
The increasing nixmberlof volixmes.in which a phase
separation is possible
results in refining of the grain. The'conclusion was made
that drawing
raised hardness more than rolling with the same reduction.
This seems to
be due to the specific effect-of different texture types and
a more com-
plex stress patternin drawing. The higher 2nd-order
distortions value
after drawing confirms this assumption. It seems that the
main factors
determining the high strength of-coldworked and aged
specimens are: de-
composition of the supersaturated solid solution with the
formation of
very disperse phase particles; refining of the mosaic
blocks; the usual
growth of the blocks in agingat 7000 and decrease of the 2nd
order distor-
tions. the intensity of these processes is low, which might
be con-
Card 3/6

20256
S114816010 00101110131015
The effect of workhardening on the .... A161/AO30
neeted with a simultaneous deoompoeition prooess and formatioh Of
Phagag
that atd oplitting the blaaks nd raising the 2nd order distortional
iia it
with inverse processes. Coagulation of phases in wonkhardened specimens
within single blocks (that
obviously
refined for long time),
goes on
stay
mainly on account of,additive separations from a solid solution. There
are
7 f igures.
ASSOCIATION: Moskovskiy%institut stali (116scow steel institute)
SUBMITTED: Febr. 25, 1960.
Figure 1: Structure af tdr qir6riching from .10800C, 8 hours
holding and air cooling. X 25,000.
ZIA, El"N..;1",
, rs-

20256

S/14e/60/000/011/013/015
The effectIof workhardening on the

Al6l/AO30
Figure 3r Structure after quenching from 1

0800, (ai'r)
and
aging for 50tOOO min in 7000- Y,1000-

!N3

4,'~
eA

6~

vwt

4: (1) After quenching from 10800

g in 700 for 5000
(air) and agin
Figure
(2) same after aging for.30,000 min.
min

X 25-000-
;

Card 5/6

2025,6
S/148/60/000/011/013/015
The effect'of Workhardening on the .... A161/AO30
Figure 6 (1) Rolling with 50 % reduction, no aging; (2) rolling
with 50 %
reduction, aging in 7000 for 5000 min; (3) same, after 30-000 min
aging.
x25PO00-
A,
NT
U
ZA
Card 6/6

KACHANDV, LL; SMSMSKIT, A.I.g MSIN, a.A.;
BMNSHTRN, K.I..
What should a modern astallographic microscope be
like?
Z&T.lsb. 26 no.6:770-773 160. (KM 13:7)
le Fauchno-Iseledovatel'skiy I sksperimentallrWy
inmtitut
podsh1pnikovoy prouWahlennosti. (for Kaohanov and
SprisheT-
skiy). 2. TSentralluaya. zavodskaya laboratoriya
Ziatoustov-
skoRo metallurgicheakogo savoda imeni L.T.Stalins,
(for
Khasin)* --3- Mosicovskiy institut stalt, im.
I.V.Stalina
(for Serushtevu).
(microscope),

5/032/60/026/009/003/018
B0151BO58
AUTHORS: Myuller, N. N.9 Bernshteyn, M. L.
TITLE: Application of the Microscopic Method for Studying
Structural Characteristics of Real Crystals N
PERIODICAL: Zavodskaya labo ratoriya, 1960, Vol. 26, No. 9,
PP- 1034 - 1086
TEXT: The structural characteristics of samples from refractory
aus-
tenitio 0395 (E1395) steel (16% Cr, 25% Ni, 6% Mo, 0.1-0.2% N21
up to
0.1% 0), from the refractory DM437 (E1437) alloy of the type
"nimonik-80",
and from metallic deformed chromium, were microscopically
investigated.
The BI395 steel was hardened at 1200'C, oold-formed, and
subjected to
aging for various periods at from 5000 to 7000C. After
differential
thermal pre-treatment, the polished sections were
electrolytically
etched. On the basis of photographs (Fig. 1) of the
microstructureg it
is stated among other things that the microscopic picture
obtained is
to be explained by the dislocations of plastic deformation. The
E1437
Card 1/2

Applioation of the Microscopio Method for
8/032/60/026/009/003/018
Studying Structural Characteristics of Real B015/BO58
Crystals
alloy also underwent thermomechanical pro-treatment and
electrolytic
polishing. The structural pictures (Fig. 2) also show
"pitting beads" at
the grain boundaries, like in B1395 steel, and it is stated
that at first
gliding only takes place on grains suitably oriented in
correspondence.
The etbhed spots are in no connection with a possible phase
formation.
Metallic deformed chromium underwent "thermal etching",
i*e.y heating in
the MBn-2 (MVP-2) furnace in helium- or argon atmosphere at
15000C for
12 or 24 hours. The influence of inclusions on gliding can
be seen in
Fig- 3 and it follows therefrom among other things that the
deforming
influence of inclusions on the configuration of the gliding
structure is
also visible at some distance from the inclusion. The
change of the
direction of gliding at the grain boundaries of metallic
chromium is
shown in Fig. 4. The present experiments showed that a
propagation of
deformation from one grain to the other does not take place
in chromium
in any base, which is in accordance with the brittle
character of ohro-
mium rupture. There are 5 figures.
ASSOCIATION: Moskovskiy institut stali (Moscow Steel
Institute)
Card 2/2

BURSHOUN, M.L.. dotsent. kmd.tekbu.nauk; MILAMOTA,
X.N., iuMs
Iffect of susten1timIng conditions on the tendency
of steel
toward temper brittleness* Sbor*Inst*stall
no*39:297-305
160. (MM 1317)
1. Kafedra met4lovedenlys I tormicheskey obrabotki
Moskovskago
ordoza Tmdovogo Xmnogo Smaimmi Institute, stall
imeni. I,T.
Stalim.
(Steel-BrIttimess) (Impering)

U&MIffNo X.L.,, dotsent,, kwA,t9khn,n%uk; IRZXMW,
G.I.0 Who
Affect of texture on the nwhaMcal properties of IhM
nickel-chromimmi-iron alloys* Mmr.Instost&ll no.39s
345-361 160, (XIIA 13:7)
1, ZiLfedr& metall"odenlya I Uruicheskey obrabotid
Moskovskogo
ordems Trudovogo lmwV Zaament Instituta @tali In*
I9T9
(Nickel-chromium-Irom alloys-Cold workiv4g)

8/137/62/000/001/152/237
A006/A101
AUTHORSs Bernahteyn, M.L., Trubstakova, R.I.
Tr=: I& effect of admixture of now elements on the proportion of
nickel.;
chrome austenite alloy
PERIODICALt Referativnyy zhumal..Netallurglya, no. 1, 1962, 42,
abstract U296
(V -sb. "Stal"', Moscow, Notallurgizdat, 1961, 462 - 468)
Mmi The authors studied the effect of m1oroadmixtures (in %) of B
0.005,
Nb 0-
..5, Ca 0.1, Zr 0.2, Oe 0.01, on the structure and properiles-of
aZ36XTID
(N36MiTfu) type alloy. . It was established that the admixtures
refined the
crystillites 'in the cast metal, reduced the zone of columnar
crystals (in particu-
lar Ce) increased surface tension (in the order of increase: 09,
Zr, Ca, B) raised
the temperature of maximum ductility (in particular B), increased
the deformation
resistance (in particular Zr and Ca).. The admixtures.affect the
aging process due
tQ__lesser diffusion into an additionally alloyed solid solution,
and also due to
the changes in theccomposition and nature of carbide phases when
adding Nb, whose
effect In the greatest. The authors established the effect of
admixtures on in-
Card 1/2

8/137/62/000/001/152/237
The effect of admixture of some elements A006/A101
ternal friction, measure d by the method of torsion oscillations
during continuous
heating up to 8WOC. Admixtures (in particular Zr and Ce),
increase creep resis-
tance at the first stage.
Ye. Bukhman
[Abstracter's note: Complete translation]
Carf 2/~

26581
S/129/61/000/008/014/015
E073/E535
AUTHORS: Ajqtaf'.'_y*#a.9 Y*. V. , Candidate of Technical'Sciencen,
Bernah**~rn, M.L. . Can-didate of Techni-cal Sciences.
_KiWfn~, ~..~,Doctor of Technical Scieftceb,
Katok, A.M., Engineer and Txypina, Ye. D., Engineer
TITLE: Strengthening'af alloyed constructional steel by
thermomechani.cal troatment
PERIODICAL: Metallovedeniye-i termicheskaya obrabotka metallov,
iq6l,.No.8,' PP-54-56 +' 2 plates
TEXT: The- authors have tried- out the effect of thermomechaaLcol
and thermo -me i.4hau i eel -66.gnat i c tireatment of the steels
10-0XIHSA
(4OKhlNVA) (0,39% C, 1.43% Cr, '1-59% Ni. 0.8% W) and 31'9143A
(37KhN3A) (0.40% C, 1.3% Cr, 3.9% NO. From annealed steel, flat
specimens,of various thicknesses were produced, all of which wer
then deformed to a final thickness of 3 mm. The specimens were
heated at 930-9500C for*20'min and, following that, they were ho:
rolled on a two-high mill or, alternatively, prior to rolling they
were placed into a furnace where the temperature was maintained at
540 to 56oOc (steel 4OKhlNVA) or 470 to 480*C for the steel
Card 1/4

26581
Strengthening of alloyed S/129/61/000/008/014/015
E073/E535
37KhN3A and held at these tempetatures for 3 min. After rolling,
kt,-,
the specimens were oil 4uenched. However, the specimens which t-,
were subjected to intermediate isothermal soaking were air
quencheil.
Some-of the specim6fas'iriike quenched in a magnetic field
produced,
by a-soleaioid,and'ib spaced that all the specimens were under
equal
magnetic...conditions. Th-e field strength was low. about 1300 Oo,
and,therisfore the influence of the thermomagnetic treatment was
not
fully apparent. The quenched specimens were subjected to low
te"erature temperifig-at 100 and 2000C with a holding time of
2 hours, followed by--c661ing'in air. Prior to the experiments, the
speci.mens were.Istfraight6hid and also ground along the contour
and
along. the. surface. 'Fukth-eir'-experiments were cArried out on
specimens.*hich.prior to heating were ground and then quenched
whilfit
inside pfinches.-* As-a k'esult of this the mechanical properties 2
improved. - Fig*3 shows the mechanical properties (HRC CY , kg/mm
Y 6, % vs. degree bf'd4f6rmation, %) of the steel 37K~NA after
th6rmom6ch6ni4~al*,treatiiiiiit"In accordance with the following
regime*.-
1 - heating'tei 9300C.",'deformation (80% reduction),' immediate
quenching, tempering -it 1000C; 2 - same an (1) except that
tempering
Card 2A

S126581
Strengthening of alloyed 129/61/000/008/014/013
w & t 200OCi 3 heating to 9300C follow7d,by cooling down to
4;04~ deformation-and,tonporing at 100*C - same as (3).
tempering at 3000C. Pok- comparison the appropriate values
obtained by. ordinary heat treatment are shown by A horizontal
line with, a. shaded aJrea (at the left-hand side of the plot).
The following conclusions are arrived at3
1. After thermome6hanicai treatment both steels showed stable
UTS values of 245-255 kg/MM2..with relative contmctions of 25-30%.
2. The high mechanical proportion after thermomechonical treatment
are attributed to the high degree of dispersion'and also to the
fict that some structural elements are oriented.
3. From the technological point of view, the thermomechanical
treatment with forming'at temperature a :bove Ac3s t;re favourablel
such treatment-yields an optimum combin tion of ength and
ductility.
4. Application of a magnetic field during austenite-martensite
transformation leads to More uniform mechanical properties and a
slight increase in strength.
There.ar6 3 figures and 2 Soviet references.
Card 3/4

M ML kand.tekhn.nauk
"Theory of creep and durability of metals" by I.A. Oding and
others. Reviewed by M.L. Bernshtein. Metalloved. i term.obr.
met. 4o.12:53-54D 161. (MRA 14;:L2)
(Creep of metals)
(Oding, I.A.)
it

S/737/61/000/000/008/0101.
AUTHORS:,._~~~~~betskova, R.I.
----- -TITLED-. Effect of small-addiiions of some elements on the
properties of a
NiGraustenite -alloy.-
SOURCE: Stall, sbornik statey. Ed.byA.M.Yarnpoll skiy. Moscow.
1961,462-468.
TEXT: The paper reports an investigation of the effect of small
additions of B
(0. 005%)o Nb (0. 5%), Ca (0. 1%6), Zr (0. 2016), and Ce (0. 011/6)
an the properties of a
NiCr austenitic alloy of the type of H36XTI-0 (N36KhTYu) with an
elevated 0 con-
tent. The alloy was fused in a 55-kg HF furnace and top-cast into
10-kg cast-iron
molds. W Mo thermocouples measured the temperature (T) of the liquid
metal.
The deformability of an alloy with given additions was measured by
the hot-twisting
method at 900-12000C. Other parts of the ingots were forged into
rod-shaped test
specim- ens. The aging of specimens quenched at 12000 was
investigated at 700-8500
by means of dilatometry, electric- resistance meavurement during
contiriaous hcat-
ing to 12000 and cooling, hardness testing, and microstructural
analysis. High-
temperature relaxAtion phenomena were studied by internal -friction
and creep
measurements. The effect of the additions on the surface tension-was
ascertained by
measurements of the angle of groves on microsections heated duti~ig
4-~.6 hours.to
.,ard 1/3

Effect of small additions of some elements. S/737/61/000/000/008/010
about 12001 M a vacuum of about 10-5mm Hg. Macrostructural templet
analysis
showed that small additions reduce the size of the crystallites in
the cast metal and
decrease the extent of the zone of columnar crystals. The sequence of
effectiveness
is: Ces Zrt Bt Nbo and Ca. The surface-tension experiments (procedure
and
statistical numerical results are detailed) show all additives except
Nb to bo surface-
active in the following order of diminishing activity: B, Cat Zr, Ce.
Correlation
with V.K.Semenchenkols theoretical calculations (no reference given)
is good, ex-
cept for a reversal of the sequence of B and Ca. The hot-twisting
test evinces the
greates plasticity at 10001G. Small additions increase it at higher T
in the same
order of effectiveness as the surface-tension tests. The
dilaton-letric curves show
two transformations: An irreversible volume reduction and hardening
at 500-6000
and a reversible volume increment at 700-9000, accompanied by
softening engendered
by coagulation and reverse dissolution of the phases. The additions
do not affect
the hardening but shift the coagulation and reverse dissolution
toward higher tempe-
ratures (especially Nb and Zr). Age-hardening is favored by
additirans (especially
Nb, B, and Zr) which, apparently, modify the compGaition of the
hardening phase
and which, also.- impair the diffusion in the parent solution, which
retards phase co-
agulation. The sequence of effectiveness in this respect does not
appear related to
the surface -activity sequence. Internal- friction measurement on
12000-quenched
specimens was performed by the tor sional- vibration method under
continuous heat-
ing to 8000. A sharp grain-boundary peak appears at 550-750'.
Additions of Bat
Card Z/3

Effect of small additions of -some elements... S/737161/000/000/008/010
Ca. and Zr reduce the height of the maximum and the slope of the descending
branch
of the curve. At temperatures beyond 7500 the internal friction increases
further.
Creep tests show that small additions produce a clear-cut increase in creep
strength
in the "first stage" of creep. The creep-strength effectiveness sequence (in
descend-
ing order) is Zr and Ge (nearly equal), Cat B, Nb. The results of the
internal-
friction and creep tests suggest that the refining action of the addition
raises the
strength of the boundarie-s. Simultaneously the surface-active effectiveness
of the
elements appears to lead to an undesirable lowering of the boundary energy of
the
grains which may lead to flow processes near the boundaries. Despite the
lowering
of the grain-boundary peak of the internal friction and the increased
creep-stability
of alloys with additives, the shapes of the curves indicate that
already-refined alloys
with elevated surface energy will be more resistant to grain-boundary f1lix
(slippage)
under the simultaneous effect of high temperatures and stresses. There are 3
figures; no references.
ASSOCLATION: None given.
Card 3/3

ALFEROVA, N.S.,, doktor tekhn. nauk;~~ kand. tekhn.
nauk; BLANTER, M.Ye.,, doktor tekhn, nauk;
BOKSHTEYN, S.Z.,,
doktor tekbn.nauk; VMOGRAD, ILI.,, kand. tekhn.nauk;
GAMOV.,
M.1.9 inzh.; GELLER, Yu.A.,, doktor tekhn. nauk-;
GOTLIB, L.I..,
kand. tokhn. nauk; GRDINA, Yu.V.,, doktor tekhn.nauk;
GRIGUOVICH, V.K., kand. tekhn. nauk; GULYAYEV,
B.B.,, doktor
tekhn. nauk.- DOVGALSVSKIY, Ya.M... kand. tekhn.
nauk; DUDOVTISEV,
P.A., kand. tekhn. nauk [deceased]; KIDD, I.N..,
doktor tekbn.
nauk; LEYKIN, I.M.9 kand. tekhn. nauk; LIVSHITS,
B.G., dok-tor
tekbn. nauk; LIVSHITS., L.S,p kandstekhno nauk;
LIVoVp M'.A.Y
kand. tekhn. nauk; MEYERSON, G.A.,, doktor tekhn.
nauk;
MINKMIICH,'A.N., kand. te'k-hn. nauk; NATANSON,
A.K.., kand.
tekhn. nauk; NAKHIVIGV, A.M., inzh.,- NAKIMM,
D.14.., kand. tekhn.
nauk; OSTRIN, G.Ya., inzh.,- PANASENKO, F.L., inzh.;
SOLODMIN,
A.G... kand. tokbn.nauk; KH31.IUSHIN, F.F.., kand.
tekhn. nauki
CIMUITASHKIN, V.G., kand. tekhn. nauk; YUDIN, A.A.,
kand. fiz.-
mat. nauk; YANKOVSKIY, V.M., kand. tekbn. nauk;
RAKHSHTADT,
A.G.p red.; GORDON, L.M., red. lzd-va; VAYNSHTEY14,
Ye.B., tekhn.
red.
[14otalloIgrap.brand theIbeat troatment-of
stool]Metallo-
vederAe: i tohdcb~skaia obrabotka stali 0-
spravochnik.
i9de2ev Peker,~ I dope Pod red., M.L.Bernahtsina i
A.G.
Rakhobtadta. Hookwa., Metallurgizdat. Vol.2. 1962.
1,656 P. (MIRA -15:10)

33462
S/129/62/000/001/005/011
E073/E483
AUTHORSi Bernshteyn. M.L., Candidate of Technical Sciences,
Demina, E,L. and Safonova, K.E., Engineers
TITLE. Thermomechanical treatment of ball-bearing steel
PERIODICAL. Metallovedeniye i termicheskaye- obrabotka
metallov,
n0'19 1962, 23-28
TEXT~ The authors investigated the influence of thermo-
me--hanical treatment on the structure and properties of ball-
bearing steel WX15 (ShKhl5) (1% C, 1.3% Cr, 0.3% Mn, 0.2% Si,
0.01% S, 0.02% P). Cylindrical and,flat specimens were deformed
by rolling at a temperature above AC3,total reductions
(estimated
by means of a logarithmic formula) of 5, 109 259 50 and 80%
being
attained in a. -single pass. The cylindrical specimens were
tempered at 140, 240 and 44o,Oc for 4 hours. The flat specimens
were tempered at 2400C (24 hours), 450, 500 and 550*C (30 min).
Air cooling was applied in every case, X-ray investigations
were
made on specimens cut from the centre of the rolled and
quenched
specimens that had not been subjected to mechanical tests.
Card 115

33462
S/129/62/000/001/005/011
Thermomechanical treatment ... E073/E483
Bend-in& tests on cylinch-ical specimens (N.I.Dolshenko
participated
in these tests) indicated that a considerable increase in
strength
and a sharp increase in ductility were obtained as a result
of
thermomechanical treatment. The results obtained with 180 mm
long,
4 mm thick specimens, subjected to thermal or
thermomechanical
treatment followed by tempering for 24 hours at 2400C,
indicated
that if the thermomechanical treatment is applied under
optimum
,zondition.s. material can be produced which even under
unfavourable
test, c-onditions will exhibit banding strength of 400
kg/mm2,
as compared with 140 kg/MM2 for specimens that had'been
subjected
to conventional heat treatment. Bending tests on flat micro
specimens yielded similar results. These specimens were
subjected
to the following treatments heating to 930% for 20 min,
reduction
by rolling in a gingle pass with reductions of 7, 25, 65 and
90%,
immediate quenching in oil, followed by tempering at 4500C
for
30 m1n, For comparison, a batch of specimens was subjected to
the same heat treatment without plastic deformation, In the
latter case the banding strength Increased to 100 kg/mm2 9
against
Card 2/5

33462
S/129/62/000/001/005/011
Thermomechanical treatment ... E073/E483
320 kg/mm2 attaine&:Ln specimens deformed to 90% r4duction;
in addition, the thermomechanical treatment brought about an
almost four-fold increasein ductility, which is particularly
Important since this steel had a strong tendency to brittle:
failure. It was found that the properties imparted to steel by
thermomechanIcal-treatment were retained at tempering
temperatures of 500 and 550*C- The strengthening effect of the
work-hardening during thermomechanical treatment is very stable
and this is attributed to the fact that plastic deformation
produces a particularly fine structure of the austenite which, in
turn, ensures high dispersion and submicroscopic nonuniformity of
the subsequently formed martensite. It Is also possible that
some texturing occurs. X-ray structural investigations show
that the density of crystal lattice defects increases with
increasing degree of deformation during thermomechanical
treatment. The actual values after ordinary heat treatment
and after thermomechanical treatment with 90% redhction were,
respectively: 2.0 x loll cM2/cm3, 3.35 x 1011 CM21cm3 after
Card 3/5

33462
S/129/62/000/001/005/011
Thermomechanical treatment ... E073/E483
tempering for 24 hours at 200*C; 1.49 x loll CM2/cm3,
3.24 x 1011 cm2/cm3 after tempering for 2 hours at 3000C;
7.94 x 1010 cm2/cm3 after ordinary heat treatment;
19.3 x 1010 cm2/cm3 after tempering at 400% for 2 hours-.
The size of -the regions of coherent scattering decreases with
increasing deformation. Stresses of the second type in
thermomechanically treated specimens tempered at 400*C decrease
monotonously with increasing deformation. The results-obtained
indicate that thermomechanical treatment with high degrees of
deformation reduces the influence of the tempering temperature
on
-the block dimensions which, in the case of smaller blocks,
.Increase at high tempering temperatures only. It is possible
that this explains, to some extent, permanence of the-.effects
of
work-hardening and reversibility of the thermomechanical
treatment. There are 5 figures, 3 tables and 4 references,
3 Soviet-bloc and 1 non-Soviet-bloc. The reference to an
English language publication reads as follows;
Card 4/5

33462 ~
S/129/62/000/001/005/011
Thermomechanical treatment ... B073/E483
Ref,2: J. K. Williamson R. Smallman. Phil. Mag.1 jL956.
ASSOCIATION: Moikovskiy institut stali
(Moscow Institute of Steel)
Card 5/5

L 05719-67 IJP(c) JDAN/W
ACC NRs AR6014354 (.4//g SOURCE CODE1
IM/0277/65/000/011/0010/00-10
AUTHORSt Kontor, L. ya.; Zaklwova, V. L ; Bernqhteyng_p~
L,1_7pher. ukhaq L, G,
TIM-: In Investigation of 11&-tGmPGratur8 ther =mechanical
treatment of bearing
.af. zh. kashinostmitel,Z779 =tWda_1.T9 konsum)&.sii I raschet
detalay,
mashin. Gidroprivod., Abs. 3-1.481.81 Z
REF SOURCE: Tr. Vass* no-io konstrAte-tokhnole in-ta.-pods
LpAik.-Prom-sti., no*
4(40), 1964 12-a-
TOPIC TAGS% bearing steel', metallurgic; researchj, MA
"argiz==" 9 Wnlo steel
structure / ShKhl5 steel
ABSTRACT: The influence of the high-tempo t thermomechanical
treatment (HTT)
ga ure
on the structure and properties or ShKhl5lT3teel has been
investigated. The HTT
process involves heating in the interval of 910-1000C,
deformation by rolling out
to 10-50%, water or oil. ggenchingf/and tempering. A control
group of specimens
was subjected to standard treatmento Applied at optimal
conditions, HTT improves
several properties of ShKhl5 steel. An experimental technique
of applying HTT to
bearing rings has beer. developedj, and a number of ball
beariMW/ana roller bearings
hae- boon produced for experimental 12u"os sa *15 illu
trntions. Bibliograpby of
6 titles, fl!ranslation of abstraotT
UDC:

slq 1 14 1
33468 i
S/129/62/000/001/011/011
Z193/Z383
AUTHORS: Lozinski3r, MiG., Doctor of Technical Sciences,
P.!2EAKh+GV=_ M4., Candidate of Technical Sciences
and Vershinskaya, TiV.,-Zngineer
TITLZ: Polygonization of molybdenum studied by high
temperature metallographic methods
]PERIODICAL: Metallovedeniye i termlcheskaya obrabotka metallov,
no4 1, 1962, 57 - 64
TEXT: Owing to the resultant formation of fine inhomo-
geneities of the structure and increase in the recrystallizAtion
temperature, polygonization of metals brings about an impro;,e-
ment in the mechanical properties, both at room and elevated
temperatures* This is particularly imRortaut in the caselof
Mo, which is mainly used in high-temperature applications and,
consequently, it in important to establish heat- and mechanical-
treatment procedures which would ensure polygoniz4tion of this
metal and its alloys. Hence the present investigation, in
which high-temperature metallographic methods such as described,
Card 1//

33468
S/129/62/000/001/011/011
Polygonization of .... 2193/9383
for instance, in Ref. 6 (M.G. Lozinskiy and N.Z. Pertsovskiy
-
Izv. AN SSSR, OTN, ter-1ya Metallurgiya i toplivo, no. 1,
1961)
were used. Experiments were conducted on vacuum-melted Mo
containing small additions of T! and Zr which constituted a
solid solution and in which no solid transformation of any
kind
took place. The\cast ingots were first hot-forged and then
hot-rolled to 3 5 mm thickness, after which the material was
annealed at 1 5;0 OC for one hour. Part of the annealed strip
was rolled at 600 OC to 5j 7, 9 and 13% reduction in
thickness
and specimens of both annealed and work-hardened-alloys were
used for taking hardness measurements at 1 050, 1 100 and
1 150 OC. In the other series of experiments,
electrolytically
polished test pieces of Annealed material were extended in
vacuum at a constant rate of strain at 1 050 and 1 150 OC and
after attaining elongation of 3, 6 and 13% were maintained
under a
load, photomicrographs of the surface of the test pieces
being
taken at various stages of this treatment. X-ray diffraction
analysis was also carried out on test pieces stressed at
ele*ated
temperatures. The results obtained can be summarized as
Card 2/'?,"~~

33468
S/129/62/000/001/011/011
Polygonization of .... El93/E383
follows.
1) Hot hardness..of the alloys studied increases with
Increasing
degree of preliminary plastic deformation but the longer the
loading time used during the hardness measurements, the lowor
is the value of hardness obtained. This is illustrated in
Fig. 2, where the Vickers hardness (HV) of various specimens
is
plotted against the loading time (min), the degree of
preliminary
plastic deformation (%) being indicated on each graph;
experimental points denoted by circles, triangles and.dots
relate, respectively, to test temperatures of 1 050, 1 100 and
1 150 C- It will be seen that an anomalous increase takes
place in specimens preliminarily rolled to 9% reduction and
that the hardness of specimens de ormed to 13t reduction Is
higher at 1 150 0C than at 1 050 9C or 1 100 C.
2) The increase.in hardness with rising temperature is
relatively small.in specimens deformed to 5 and 7% reduction
and-large in more heavily deformed material, this increase
being particularly pronounced in specimens given 9% reduction,
which indicates that this treatment brings about
polygonIzation
Card 34;~,,-

33468
S/129/62/000/001/011/011
Polygonization of .... 12-193/9383
2
of the alloy. In Fig- 3 the decrease in hardness (A H, kg/mm
is plotted against the test temperature, the degree of
preliminary deformation being Indicated by each curve.
3) The microhardness of the alloy at high temperature also
varies with loading time. This is demonstrated in Fig. 4,
where the microhardness (HV, kg/MM 2 i; Slotted against the
lodin.g time at 1 050 (graph a) and 1 15 C (graphG), the
degree
of-preliminary deformation being shown by each curve. It will
be seen that the0microhardness of all work-hardened specimens
tested at 1 050 C decreases monotonically with increasing
loading time; the curves for specimens given 9 and 13%
reduction
and tested at 1 150 0C show a maximilm at 30 and 80 min,
respectively. The maximitim increase In microhardness with
increasing loading times is shown by a specimen deformed to 9%
reduction and tested at 1 150 OC-
4) The results of X-ray diffraction analysts show that
fragmentation of blocks in the course of plastic deformation
is
a characteristic feature of Mo and that the degree of
Card 4/Y,-

Polygollization of ....
33468
5/i2q/62/ooo/ool/011/011
fragmentation can be assessed from the increase in the width
of the X-ray lines. In-Fig. 6, the increase in the width
(Plo-3 radians) of the (211) lines Is plotted against the
de-ree of deformation at temperatures indicated by each curve.
it will be seen that a maximum degree of polygonizatlon Is . I
attained in the materiitl,extended.to.9% elongation at 1 150 0C_
-If, however a specimen in this condition is held--undez- a-
-load. at 1 lio0C for 80 min, the. X-ra.y reflections become.more
diffuse, indicating that this treatment brings about an
increase in the dimensions of blocks.
There are 8.figukes and 10 references; 9 Soviet-bloc. and,
I non-Soviet-bloc. The English-langu.agie reference.mehtioned
is: Ref. 4: Cahn, R.W. - Proco Phys. Soc.,-A63, 19500-
ASSOCIATIONS: Institut mashinovedeniya GKAMSM SSSR
(Instituis of Machine Science of GKAMSM USSR)
Moskovskiy institut stali (Moscow Institute
of.Steel)
Card 50
tj

S/133/62/000/004/008/008
A054/A127
AUTHORS: Bernshteyn. M.L.; Rakhstadt, A.G.; Docents, Candidates of
Tech-
n1cal Sciences
TITLE: 7hermomechanical treatmeat of spring steel and its
reversibility
PERIODICAL; Stalt, no. 4, 1962, 346 - 348
TEXT: Steel alloys used for #rings must display resistance to plastic
de-
formation and resilience. To improve the properties of these alloys
tests were
carried out to include a thermomechanical treatment in the production
process of
laminated and'helical springs. 55XrP(55KhGR) and 65r (65G) steels of
the fol-
lowing composition were used in the tests: 55MR grade steel (in %):
0.53 C;
0.35 Si; 1.0 Mn; 1.1 Cr; 0.003 B; 0.03 Ti; 65G grade steel: 0.64 C;
1.05
Mn; 0.25 Si. The specimens of the first steel grade were heated up to
9200C,
rolled on a two-high mill with reductions of 15, 25, 50 and 75% for
one pass,
then straightened under a press and air-cooled which, for this grade,
was eq7ai-
valent to complete hardening. After this the specimens were tempered
at 100,
200, 250 and 3000C for 40 min. The 65G steel gra:de specimens were
treated in 4
different ways: I) Refining and oil hardening at 8700C and tempering
at 6500C
Card 1/3

S/133/62/000/004/008/008
Thermomechanical treatment of .... A054/A127
for 1 1/2 h; II) refining + cold deformation (rolling) with a
reduction of 12.5%
+ oil hardening at 8700C + tempering at 6500C for 1 1/2 h; III)
refining + roll-
ing (25%) + oil hardening at 8700C + tempering at 6500C for 1 1/2
h; IV) heating
to 1,OOOOC + rolling (25%) quick oil hardening + tempering at
6500C for 1 1/2 h.
It was found that the thermomechanical treatment of the 55KhGR
steel)vade (re-
duced by 25 - 50%, hardened and tempered at 250 - 3000C)
considerably increased
the strength and ductility of this spring steel. The
thermomechanical treatment
has a stabilizing effect on its characteristics, the practical
importance being
that this stabilizing effect on the steel can be preserved after
additional high-
temperature tempering, repeated hardening and low-temperature
tempering. \The re-
peated heat treatment imparts to the steel specimens, after
processing on metal-
working machines, the same degree of strength and increased the
ductility as ob-
tained during the thermomechanical treatment. In this way it is
possible to ap-
ply this treatment to many steel grades at the rolling shop, in
the last stage of
hot rolling. After high-temperature tempering the 'metal can be
subjected to me-
chanical processing and subsequently to a final heat treatment in
the engineering
plants. It was found that the heat treatment requires rapid
heating. A prelimi-
nary cold deformation of the 65G steel grade prior to hardening
and tempering re-
sults in greater strength than if no worldiardening is applied.
The mechanical
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S/133/62/000/004/008/008
Thrermomechanical treatment of .... A054/A127
-characteristics of 65G steel grade, after the four heat treatment schedules
given
above were the following:
CIB. Cr., r:z1X.M&% %
45.8-47.9 19,1-17.6 57-54
H 81,6-78.0- 53.5-54,0- 14,6-13.7- 54-53-
84,1 66.1 13.0 49
111 84.7-85.5 65.4-66,4 13.2-13.0 50,4-49.5
IV 85,2- 89 72,3-74,7 13,0-12,7 49.7-48,4
The fact that the effect of workhardening is maintained and transferred in the
65G grade steel after hardening and high-temperature tempering was also
apparent
from x-ray structural analyses of the fine-grained structure of specimens sub-
jected to the four versions of heat treatment. They showed a considerable
physi-
cal widening of the diffraction lines in specimens which were workhardened.
There is 1 table.
Card 3/3

S/129/62/000/006/005/008
E073/E435 I
AUTHORS: 'Chudnovskaya, Le'A., Candidate of Technical Sciencest'
Bern n ir Candidate of Technical Sciences,
Shevyakova, L.G., Engineer
TITLE: Thermomagnetic and thermomechanical-magnetic, treatment
of tool steels
PERIODICAL: Metallovedeniye i termicheskaya obrabotka metallov,
no.6, 1962. 36-39
TEXT: The influence of these treatments on the mechanical
properties of steels X~-,r(KhVG) and P18 (R18) was studied. The
thermomagnetic treatment consisted of: 1) quenching austenized
specimens in an oil tank placed between the.POI;s of an electro-
magnet which produced fields up to 5000 Oe or in a tank placed
inside a solenoid which produced an alternating field of up to
1200 Oe; 2) applying an electric field to the specimen during the
entire process of tempering, i.e. during heating up, holding.and
cooling. Thermomechanical-magnetic treatment: specimens of R18
steel, 20 mm long, 1.2 mm, diameter, were heated to the quenching
temperature and then air-cooled inside a magnetic field of up to
Card 1/2

Thermomagnetic and
s/129/62/000/006/005/008
E073/E435
2000 Oe. The results indicate that application of a magnetic
field accelerates the austenite to martensite transformation and in
s6me cases brings about the formation of a crystallographic
texture. Thermomagnetically treated specimens of KhVG steel
tempered at 1750C with the application of an alternating magnetic
field had bending strength values over 300 kg/mm2, i.e. higher
than for specimens tempered without the use of a magnetic field.
The, strength of specimens of R18 steel was about 20%/ higher after
thermomechanical (5% deformation)-magnetic treatment than after
ordinary heat treatment. The average breaking torque of a
7 mm twist drill (after the usual hardening and tempering) in an
a.c. magnetic field -was 1610 kg/mm2 as compared with 1250 kg/mm2
for an equal twist drill subjected to -treble tempering at 56o*c
for one hour without applying a magnetic field; the wear
resistance was about 15% higher. There are 4 figures.
ASSOCIATIONS: VNII
Moskovskiy institut stali (Moscow Steel Institute)
V-
Card 2/2

0985
S/659/62/009/000/019/030
10031IM3
AUTHORS: Demina, E. L., Tai Tunkfa and !nsh ~nM- L.
TITLE- The inftence of cold-working and of alloying on the
crystal structure and on the propet-
ties of nickel-ban heat resisting alloys
SOURCE, Alrademiya nauk SSSR. Institut metallurgii.
Issledovaniya po zharoprochnym splavam
v. 9. 1%2. Materialy Nauchnoy sessii po zharoprochnym,
splavarn (1961 g.), 139-145
TEXT: The alloys investigated were quenched from 1000-1200'C,
and drawn to a 5.25 % and 75% de-
formation. Hardness, red-hardness, the mosaic structure and
internal friction were determined. It was con-
cluded from the data that internal friction increases with
increase in the degree of cold-working, and that
slip is easier along the block boundaries when the samples
with a high degree of cold-work deformation are
heated, this is due to dislocation movements caused by the
heat and applied stress. The investigation on the
effect of alloying with chromium, molybdenum and tungsten
shows that there is little strengthening of the
solid solution exoept when the alloying elements present cause
lattice imperfections by the formation of a
strengthening phaw on aging. There are 4 figures and I table.
Cafd 1/1

I r, T~ n 07"

Carl 3/4

F
I .. . . ~ --4 1 - : - . :
: . 1" : . - - ~ ; -.1
1 .1 ~ I
!4!4

S1 IL26/63/015/001/010/029
AUTHOAS t #--and $htrOme-I6.# ~N.A.
TITLE:- The Alkerie'ditery"' influence of'wiork, hardening an the
PERIODICALs Pi-siker metallov I petallovedeniyet v0 .15 tIla* Is 1963,
"T s, tl ' la.
EX "1P0 d, P stic: deformation ofton~ produce's effects on the
T
properties .Of vtee2.which-~Purvive several' phase recrys to I livat
ions.
This,cou. t e'4cstier'of test'. r
iti ac.cox tnt: for: eoults characteristic
of,-,,.~at,-ches`,-of -.induiitrial steels. ~ A study of the. effect
of:-'.
iminary. ~% per brittleness
--pre, I r~6rk hardening on-the tendency to tem
4 4oxfik) - at, e in with add It ions of No', V, Al ~ knd * B
of Ox"
sh6w'ed that'*., slome- iffee't a Oer4isted through a series of' a y
change 0" &.n0 that'.4oik'hardening,of steel in the austenitic state
a vartictiIii-ly- marked *'f f ect on the. temper brittleness 'after
harden-ing, on and on fine'structure of the ~steelo'
.The rmo-mochanl6a:lly created steels show. p6ratatent, "inherited"
effects-, for. which, tb4 following.specific features of structure
tiansf6rmatlowmachanisms in-this' treatment are responsibles
Card 1/2.
a

S/126/63/015/001/010/029
Toe tlhereditary"~:infli6nciv -of work
1~' Work hardening roduces.-grain size, the fine grains generally
survivin -g ~.a Y"~trahsforwation unle.se collective
recrystallisation
Can occ4r., 2) The texture produced by work hardening makes some
propertiew.anisotropic'O In addition to -this 11crystallografPble"
is'& "diji location" texture (noh-uniform 'distribution
of dialoc t -ions between .'.crystallographi .oilly po-asible .slip
systems
''*
i
ri*.,'each- ci*italltte *.~--and -Ja Iwo* relative to"the
polyerystal an a.
who IeY. Fin'ally,,. there is a. "precipitate## I-texture which can
ariseF.. if 'thw' symmetry ofform.-or lattice of the preciipitates in
....,lower. than that*,of the ma.tri*f . this.. can lead to
"inherited" offects
e*g _~Ih:al 0y ore- iform distribution of.-carbon ;Ind
I Steel- lih non-un
alloying !eIj0nehks persists for a -long time after the formation of
austenlte*, - omot in& the.'restoration of the "precipitate"
texture.
fi., I Pr
a er, ardenin't .There Are 6 figures and 5-tables.
ASS OtI ATIO Ns: Mookl~4ikiy.-inxtitut .8tali,:i.splavov
'ute.of'Steel and.Alloys Y
qjovcow.~ Ins it.
SUBMITTEO.s.. 'Augudt'.,
Apri1:.: 13,. - 1962. (after revision)..
Card' 2/2

s/l29j63/000/004/002/014
A004/A127
AUTHORS: Bernshteyn, M.L., Cherepanova, G.I., Ryzhak,S.S.
TITLbs 'High-temperature thermomechanical treatment of type X 8 (as)
alloy's
PER.IODICANtil~*VLtallovedeniye i termicheakaya obrabotka metallov
, no. 4,
19639 5 - 8
TEXT; The authors carried oit tests with the OX 8 (OKh8), 27 X 6
(27aS) and 47 X8 (47M) alloys to study the effect of
high-temperature
thermomechanical treatment on these alloys. It was found that high-
-temperature thermomechanical treatment of these alloys results in
a stable
strengthening which is maintained even after a phase
rearystallization with
rapid heating, i.e., the investigated alloys showed a reversibility
affect
of thermomechanical treatment. The amount of latent energy
accumulated in
the high-temperature-thermonechanical treatment procoss exceeds
that ab-
sorbed in cold deformation 'by a factor of 1.5 - 2.
Recrystallization in
the initial stages does not fully remove the strengthening effect
of high-
-temperature thermomeohanical treatment$ which increa-ses the
softening
Card 1/2

B/JL26/65/015/001/010/Q29
AUTHOAS t- Pr"Xiiie'' and $htreN10,14.0 *A*
TITLE The.-t1keeieditiryw, i~iluonce pf'ivork- hardening on the
prop* ties:* --itei
us 02
PE RIOD'' '-u P z1k*-m4tA11dv :1 pwtall'Oveden1yej,-'V~',15v' noAis
19639
ICAL.
'T v`~ C olid *a i *a.' idefo ra ation of toii, ef rtcts- an the
T
9X pro
propertioa-.of ~&.teel which surylve. several PhAserecrystiallinations.
This. couXd:`4c`c6m.at*:' acattor'of test",ripults characteristic
ndu'it *eta.- 'A stuo.0f. the''effect 6r'.'
o f..~_ba.t.chies'.
Pre lir~injii WO ,ek, hardohing on' t'he I*end*ncy to temper
brittleness
iels 4ith idditt Ions'otMo', W, d'
of at 41a 0
Wed. a eries of' a y d
im, riisted through.a.s
'harden ,ing,of 46teel An the austenitic state
had a leuilarly-- marked elrfect -: on' the. temper. brittleness'
'after
ardening, op:'.s r ji'St structure of* the: -.steel*
h t hs ~a"4
on fine
treated steels. show. Orslste.nt, Uinherited"
eff eq6te, for -whichytb4. followt gJapecif it,-featurt's *of structure
eA f6rmation-machaniams.in*,th a treatment are respons s
and t ns ible

V
4/426/63/01~~091/010/QSV
akr Inflilifti -9:r' work-
83.
hardening k6d~viis ---trikin 61 .ze'', 'th .ect ins gra' Iin's
'generally
-MQr
aurv ivin,'g'':,a: colloctlvw rie'erystallisation'
can. occur. 2) Theitexture produced by work.bardening makes some
piopik id's -,'..3). In -addition to -thimi, "crystallografpbiom
td) .cture-Aher . a- is'a -Adis'lo6ationt' textureln"oh-uniform
distribut4on
PC;'. di slo c aitions.~.betwo6n .cryst all ograp4io,ally 'possible
slip systems
I -Aeacu, :~c.rys alli .to' I a.nd,also' relative to- .the
polycrystal as a.
t
whole) -4),,PinalIy0,-th4-re. Is a.-.11pric1pitate", texture which
can
ariso if+ the, symmetky'of',form.-or lattige oU'the precUpitates Is
.',.lower than`thit.~ of ~the matriki . this can lead,to "inherited'$
offects
n, . &1*1~y ate o JL'. wh er's, n,o,. im -distribution of.-carbon
iwnd*
6 "g. n-unif6
alloying 41~ments -porslsitli .'for a long time after th6 formation
of
au late nite', proj not%ing. the, i,6 a; toration of. the precipitate
texture.
-.There. are
6 figures and 5. tables.
..-ASSOCIATION: Mdsk6v#k-Ay.1nPt itut. stali:,I~-splavoiV'-
No'sim6w.:1nititute. of Ste'li I ..And.. Alloys),
Suffldliftb- 1'62. 1 (initi
Augulit 9
ally)
'il,-43' - 1962. (after revislimi).
A
Card, 2

-9-OSHMMALl- I red.; SKAKO~ 0 Yu. A. . red.; LEVIT,
Ye. I., , red.
izd-va; ISLENVUU.-P.G., tekhn. red.
[Now electron microscopic studies) Novye
elektronnomikro-
skopicheskie issledovaniia. Moskva, Metallur isdat,
1961. 214 p. Translated from the English.
&IIIRVi6s.5)
(Electron microscopy) (Metallography) -.- -

- BERNSHTRYN M.L.; DIY TUNZU (Tal Tvuzigwf~]
Theory of transformations in nickel-bass solid solutions.
Isel.
pa, shmpr.oplav, 8tl"-155 t62, (KEFA l6s6)
(Nickel alloya.-PIstallography) (Phase rule and equilibrium)

DEKNA, E.L.; DAY TUN-FU [Tai Tlung-fu];
Effect of peening and alloying on the fine structure
and properties
of heat resistant nickel alloys.. Isel. po, sharopr.
splav 92
139-145 162. iKMA 16t6)
(Nickel alloys-Cold working) (Heat resistant alloys)

LOZINSKIYj Mikhail Grigor'ysYiQb;. NP red.; GORDON,
L.M., red.12d-va; BAYNSH 10- red.
[Structure and properties of metals and alloys at high.,
temperatures] Stroenie i svoistva metallov i splavov pri
vysokikh temperaturakh. Moskva, MetaLlurgisdat, 1963. 535 p.
(MIRA 16:8)
(Metals at high temperatures) (Metallography)
Ael.