SCIENTIFIC ABSTRACT LOZINSKIY, M.G. - LOZINSKIY, M.G.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R000930630002-8
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: August 23, 2000
• Sequence Number: 2
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

SOV/24-58-6-4/35
Elastic Vibrations Measurements as a Method of Investigating the
Thermally Induced Changes of Properties of Meta.js and Alloys
and also (curve )+) for a specimen which, after being
to 51WOC, was cooled to room temperature. The relatiol
ship between the impact strength and the duration of th6
tempering at 5WOC of specimens quenched from 90000,
10000C, and 11500C, is graphed in Fig 6. The curves on
Fig 7 show the temperature dependence of S of (1) an
untreated specimen, and (2) a specimen quenched from 1000OG
tempered for 2 hours and cooled in water. Fig 8 shows the
dependence of the height of the peak*on the duration of
the tempering treatment carried out at 3000C, 3500C2 40000
and 450oC. Finally, t~e dependence of ln 11/&,,) (where 6
is the height of the peak of untreated specimeng and
the height of the peak after tempering) on the duration of
the tempering treatment at 300, 3507 400 and 4500C, is
,&raphed in Fig 9. It can be seen tha' all the curves of
the logarithmic decrement plotted against temperature for
specimens quenched from various temperatures (Fig 5),
exhibit a peak at approximately 3500C. Since the
Card 4/7 mechanism causing the 3POC peak was completed at tempera-
tures lower than 5400C, it is concluded that this peak -is

SOV/24-58-6-1+/35
Elastic Vibrations Measurements as a Method of Investigating the
Thermally Induced Changes of Properties of Metals and Alloys
not associated with the process leading to temper emb-Zitt-
lement. Analysis of the experimental results indicates
that the height of the peak was related to the time and
temperature of the tempering treatment. An expressi3n
(Eq 5) was derived for the maximum rate of coalescence of
the precipitated carbidess Vmax = 100(n(T), %/sec. The
graph of the function?, (T) shoiH on Fid 10 is chara.-ter-
ised by two values of temperat-are T: T = To at which -.,max
= 0, and T = 9 at whic:i vmax approaches infinity. On the
basis of the results of the present investigation ths
following hypothesis was postulateds In the initial stages
of tempering the martensite formed during quenching is
partially decomposedg thus relieving the internal stresses
and increasing slightly the impact strength. Lt higher
temperature, the deccmposition of martensite is intan-
sified and the precipitated carbides are enriched in the
atoms of the alloying elements. This results in a
Card 5/7 weakening of the bond between the adjacent carbide
particles, and leads -to the pronounced drop in the impact

SOV/24-58-6-V35
Elastic Vibrations Measurements as a Method of Investigating the
Thermally Induced Changes of Properties of Metals and Alloys
strength which is typical of the first type of temper
brittleness, The most complete decomposition of marten-
site and consequent segregation of carbides takes place
at temperatures higher than To. During this stage, a
strengthening of the bond between the discrete metal
phase occurs which results in an increase of the impact
strength. At temperatures above ~1 the strength-of the
bond between the discrete particles within the grains
continues to increase, which creates conditions favourable
for further coalescence of the alloying elements and their
migration to the grain boundaries. The latter process may
be responsible for the second type of temper brittleness
encountered in the 450 to 5500G range. At still higher
6emperatures, the widening range of the solid solubility
of the alloying elements in c:A. iron permits dissolution of
these segregated impurities into the grain boundary
Card 6/7 regions; material quenched from such temperatures is
ductile because the impurities are held in the solid

SOV/21+-58-6-1+/35
Elastic Vibrations Measurements as a Method of Investigating the
Thermally Induced Changes of Properties of Metals and AlloYs
solution. Brittleness induced by slow cooling is caused.
by gradual precipitation of impurities at the grain
boundaries. These considerations led the authors to the
conclusion that the "solution-precipitation" theory is
probably the most correct of any yet expounded on the
reversible temper brittleness.
There are 11 figures and 19 references, of which 9 are
Soviet, 8 English and 2 German.
ASSOCIATION: Institut Mashinovedenniya AN SSSR (Institute of
Machine C0A0trL1at1oft- of the- AS 'USSR)
SUBMITTED; October 11+, 1957
Card 7/7
-ON

SOV/24-58-7-27/36
AUTHOR: Lozinskiy,,.M L. (Moscow)
TITLE: L
--iome Relations in the "Elastioll Movement of Alpha-cobalt
tAicrovolumes.During Heating and Stretching (Nekotoryye
zako--nomernost-L "uprugogo" peremeshcheni-ya mikroobllyemov
allfa-koballta pri nagreve i rastyazhen-*,i.)
PERIODIGAL. Izvestiya Akademii nauk SSSR, Otdeleniye teklinicheskikh
nauk, 1958, 'Nr 7, pp 134 - 135 + 2 plates (USSR)
ABSTRACT: The author refers to his investigations of the deloormation
of polyorystalline metals and alloys by high-temperature
metallographic methods (Refs 1-3). These showed that
elastic deformation of individual mierc-volumes inside
and on the surface of grains is reversible only when the
stresses.'set up do not lead to a definite energy barrier
being su'riassed. Inter-atomic forces in the a-ystal lattice
cause the displaced volumes to return. This is illustrated
schematiually in Figure 1 and by a series of photo-
micrographs (Figure 2) of the same portion of a polished
surface of grade K-000 cobalt in the course of an experi-
ment on a type IYAASh-5M installation (which has been
described in Ref 4). This series shows the appearance and
Card 1/2 disappearance of different type_- of surfa,,-e relief as the

SOV/24-58-7-27/36
Some Relations in the "Elastic" Movement of Alpha-cobalb Microvolumes
During Heating and Stretching
specimen was kept at 400 0C. in a vacuum of 10-5 mm Hg
and subjected to tensile stresses. The orystallograpbic
orientation of a given zone and its position relative to
adjacent zones can affect the tensile-stress value at
which relief is formed (Figure 3 shows the zone of a pure-
cobalt specimen where fracture took place after 15 minutes
at a higher stress value than those corresponding to
Figure 2). A chemically etched alpha-cobalt surface is
shown in Figure 4. The author concludes that his results
prove beyond doubt the existence of the"elastic" movement
and refers to B.M. Rovinskiy's work (Refs 5-7) with iron
and tungsten. He proposes to extend his own work to other
pure metals and alloys. There are 4 figures and Soviet
references.
SUBMITTEDi March 29, 1958
Card 2/2

SOV/129-58-11-3/13
AUTHORS: Sokolkov, Ye. N., Candidate of Technical Sciencev,
JeAjgakiy...~~ Doctor of Technical Sciencesand
Antipova, Ye. I., Engineer
TITLE: Structure of Grain Boundaries and Heat Resistance of
Austenitic Steel (Struktura granits zeren i zharoprochnost'
austenitnoy stali)
PERIODICAL: Metallovedeniye i Obrabotka Metallov, 1958, Nr 11,
pp 19-25 + 4 plates (USSR)
ABSTRACT: Hardening of the boundaries of austenitic grains,
detected during impact bending tests and also as a
result of static tensile stresses at liquid nitrogen
temperature (Ref 6), leads to the assumption that the bsr-de~g
is accompanied by an increase in the resistance to plastic
deformation at~elevated temperatures. Therefore, it was
considered advisable to investigate the influence of the
structure of the grain boundaries in the austenitic steel
60Kh4G8N8Y on the creep speed. After hardening from
1100-1150 C, this steel has an austenitic structure and
possesses a high impact 0strength, 30-40 kgm/cm . Ageing
in the range of 600-800 C results in separating out of
Card 1/5 a carbide phase which brings about a drop in the impact

SOV/129-58-11-3/13
Structure of Grain Boundaries and Heat Resistance of Austenitic
Steel strength to 3-5 kgm/cm 2. The deve ent of brittleness
is accompanied by inter-crystallittkisruptions. 0 It was
established that rolling of steel at 900 to 1000 C under
conditions excluding recrystallisation of austenite leads
to a reduction in the brittleness. The authors considered
it of interest to compare the established influence of
plastic deformation on the impact strength with the creep
speed at elevated temperatures. The experiments were
effected by means of the test device IMASh-5M which permits
studying the micro-structure during heating and tensile
tests in vacuum (Refs.?-9). The material was prepared for
the investigations as follows: the blanks were heated to
1200 C ando allowed to cool to the rolling temperature
(1000-1100 C). Rolling with a reduction of 25% was
effected on a laboratory rolling stand. For preventing
recrystallisation of the work hardened austenite, the metal
was cooled immediately afterwards in water, whereby the
time interval between the end of the rolling and the cooling
process amounted to no more than 0.2-0.3 see. A part of
the blanks which ~vere n8t subjected to deformation were also
Card 2/5 hardened from 1000-1100 C. Following that, the blanks were

SOV/129-58-11-3/13
Structure of Grain Boundaries and Heat Resistance of Austenitic
Steel
aged for a duration of four hours at 750 OC and then
specimens were cut out to a shape as shown in Fig.l. The
flat surface of the specimen.was ground and chemically
etched for the purpose of revealing the structure. The
etched stru8ture was conserved during subsequent heating
to 900-1000 C in vacuum and this enabled observations of
the changes in the structure during plastic deformation.
For measuring the deformation during the tests a number
of indentations were made on the ground surfacei these
were arranged perpendicular to the axis of the specimen
with spacings of 6 mm; during the tests the distance
between the individual indentations were measured with an
accuracy of + 111. The specimen was heated by passing
current direitly through it, whereby the temperature was
controlled by a thermocouple which was welded onto the
specimen. All the changes in the structure observed
during the tests were recorded by photographing one and
the same spot of the ground surface. The micro-structures
of the specimens after three heat treatment regimes are
reproduced in Fig.2, whegeby the duration of ageing in all
Card 3/5cases was 4 hours at 750 C. The test results graphed in

SOV/129-58-11-3/13
Structure of Grain Boundaries and Heat Resistance of Austenitic
Steel
Fig.3, i.e. the changes in the elongation of the steel
6OKh4G8N8V with various ini8ial structures as a function
of the best duration at 900 C and an initial load of
5 kg/mm-", show that the behaviour of the specimens differs
greatly for differing initial structures. It can be seen
from Figs.4 and 5 that in ordinary specii6ens,as well as in
specimens preliminarily deformed at 1000 C,cracks will
appear and develop along the boundaries of the austenitic
grains. The influence of partial recrystallisation at
elevated temperatures on the heat resistance is graphed in
Fig.3; a special experiment (curve 4) shows to what extent
the creep speed can Increase when crystallisation develops.
On the basis of the obtained results the following
conclusions are arrived at: For the investigated alloy
an increase in the heat resistance will be brought about by
such changes of the structural state of the austenitic
grain boundaries which result in an intensive distortion
of the preliminary plastic deformation under conditions
excluding development of recrystallisation; a decrease in
Card 4/5 the creep speed is linked with braking of the plastic

SOV/129-58-11-3/13
Structure of Grain Boundaries and Heat Resistance of Austenitic
Steel
deformation along the boundaries of the austenitic grain;
hardening of the alloy is apparently also determined by a
change in the fine structure throughout the entire body
of the grain.
There are 5 figures and 9 references, 8 of which are
Soviet, 1 Czech.
ASSOCIATIONS: Institut fiziki metallov UFAN SSSR (Institute of
Metal Physics, Ural Branch of the Ac.Sc., USSR) and
Institut mashinovedeniya AN SSSR (Institute of Mechanical
Engineering, Ac.Sc., USSR)
1. Steel--Structural analysis 2. Grains (Metallurgy)--Boundery'.la er
.Y
3. Grains (Metallurgy)--Crystal structure 4. Austenite--Metallurgical
effects
Card 5/5
21

L-07-INKly, M-C-
AUTHOR: Rustem, S.L.
129-4-12/12
TITLE: All-Union Conference on industrial use of high frequency
currents held in Leningrad. (Vsesoyuznoye soveshchaniye
po.promyshlennomu primeneniyu t.v.ch. v 6. Leningrade).
PERIODICAL: Metallo~vedeniye i Obrabotka Metallov, 1958, No.4,
pp. 61-64 (USSR).
ABSTRACT: The conference held in November, 1957 was convened by
the Leningrad Scientific and Technical Society of the
Engineering and Power Generation Industry (Leningradskoye
Nauchno-Tekhnicheskoye Obshchestvo Mashinostroitellnoy
i Energeticheskoy Promyshlennosti). The task of the
conference was to report on advanced experience, to
discuss achievements in this field outside the Soviet Union
and to evolve recommendations for expanding the use of
high frequency in industry and introduction of progressive
technology and also evolving organisational measures for
improving the quality of high frequency equipment and
apparatus. The conference included sections.for
induction heating technology, metals technology, non-
conducting materials and equipment
Candidate of Technical Sciences, M:A. Spitsyn (NII TVCh
imeni V. P. Vologdin) read the paper "New developments
Card 1/141n the field of industrial application of high frequency

129-4-12/12
All-Union Conference on industrial use of high frequency currents
held in Leningrad.
currents". In this paper he outlined the most important
trends in the use of high frequency heating between 1955
and 1957 dealing with surface hardening of components
with complicated configurations; high speed gas carburisa-
tion using induction heating; heating right through of
blanks for forging, stamping and rolling; development of
apparatus for controlling heat treatment processes and
automation and mochanisation in large batch and mass
production. Duriiur the last three years the following
technological processes have been developed which are based
on induction heating:
1. Two-frequency "hardening" of the surface of toothed
gears with average * moduli. First, heating is effected
with a frequency of 1000-2500 c.p.s. during which the heat
is generated mainly at the bottom of the tooth gap and,
following that, radio frequency is fed to the inductor
for a duration of 0.5 -to 0.8 sec for heating the tips of
the teeth. Subsequent quenching permits obtaining a
hardened layer which r6producesthe shape of the teeth.
2. Gas case hardening of toothed gears using induction
Card 2/14heating ensures a sharp increase of the speed of the

129-4-12/12
All-Union Conference on industrial use of hiGh frequency currents
held in Leningrad.
chemical-heat treatment and is used successfully in the
automobile industry.
3. Hardening of the drilling bits for use in the oil
industry.
.4. "Bright" annealing of steel strip.
5. Two-frequency heating of steel blanks for heating
by applying pressure, particularly for rolling.
6. Heating and hardening of leaf springs on automatic
machines.
7. High.speed tempering of hardened components using
high frequency heating etc. For automating technological
processes, the followinG are at present manufactured:
An automatic machine for heating and hardening of leaf
springs; manipulator for horizontal forging machines;
automatic machines for hardening of small components.
Of the new apparatus used in induction heating, the
author mentioned a stabiliser of the temperature of compon-
eats being heated, a photo-electric pyrometer with a direct
reading off of the temberature, relay for dosing the energy,
etc. Of particular interest were the data he gave on
Card 14the two-frequency heating of gears. The entire process

129-4-12/12
All-Union Conference on industrial use of high frequency currents
held in Leningrad.
takes only a few seconds and can be used in mass production
for heat treatment of gears with average moduli. Heating
of blanks which are to be shaped by applyinG pressure is
also effected by two-frequency induction 0heating using
50 c.p.s. current for heating to 700-750 C followed by
heating with high frequencies to 1100-11500C. The tvio-
frequency induction heating reduces the consumption of
electricity in the case of heating right through of blanks.
For tempering and annealing of weld joints, induction
heating with 50 c.p.s. and with higher frequencies is used.
The paper of M. G. Lozinskiy, Doctor of Technical Sciences,
Institute of-Egineering Technology, Ac.Sc. USSR
(Institut Mashinovedeniya AN SSSR) dealt with the problems
of strength of surface hardened components and the
features of high frequency heating. The deformation
detected by the author in engineering magnetic steels
"45" and 114OXII forms in the surface layer as a results
of magnetostriction caused by the a.c. electromagnetic
field of the inductor. On a smooth surface of blanks
consisting of magnetic steels which were subjected to
Card 4/14 repeated cycles of heating and cooling, "mounds" and

129-4-12/12
All-Union Conference on industrial use of hi,r,-h frecuency currents
hold in Leningrad.
"valleys" form at spacings equalling the half-wave of the
supersonic oscillations generated by the hiGh frequency.
In non-magnetic steels no such phenomenon was observed.
It was also observed that with increasing number of
cycles, heating-cooling, the diameter of the cylindrical
specimens in the heatinG zone increases, whilst -the height
of the specimens decreases. Furthermore, the author
reported on the method of G. V. Uzhik which enables
increasing the static strength up to 300%; this is achieved
by using h.f. heating of a thin layer in the zone of
stress concentrations at the surface of steel components.
Thus, for instance, cylindrical specimens made of hardened
4OX steels with a stress concentrator in the form of a
notch will be 2.5 times stronger if the notch zone is
tempered by using h.f. heating. M. G. Lozinskiy considers
that use of the method of strengthening applying h.f.
tempering of the stress concentration zones will permit
evolving specifications which would justify more rational
designs than those used hitherto.
K. Z. Shepelyakovskiy (ZIL) read the paper "On reducing
Card 5/14the hardenability as a means of achieving contour (surface)

129-4-12/12
All-Union Conference on industrial use of high frequency currents
held in Leningrad.
hardening of toothed gears of average moduli". For this
purpose a steel with low hardenability, 9A 937, was used.
Gears made of this steel, of 180 mm dia. with a modulus
of 4.2,were heated by means of an 8000 c.p.s. current of
100 kW capacity for a duration of 24 secs. The heating
was effected in a ring-shaped inductor after which the
gears were moved into a ring-shaped shower with a fixed
direction of the holes. The teeth and the rims of the
gears were subjected to hardening. The stren-th of the
hardened teeth was investigated by loading until failure.
In the case of gears made of the steel 3oxrT (after
carburisation and hardening) this load was 15.6*tons,
for the steel 5W 937 the load was 16 tons. In the case
of hardening of gears made of the steel M 937, a minimum
deformation occurs, the fluctuations along the pitch circle
after hardening amounted to 0.01-0.02 mm. In some cases
the contact strength should be increased by increasing the
carbon content to 0.6-0.7%.
I. L. Glukhanov, V. N. Bogdanov, Ye. D. Makarova,
H.F. Scientific Research Institute imeni V.P. Vologdin
Card 6/14 (NII TVCh imeni V. P. Vologdina) presented a paper on

129-4-12/12
All-Union Conference on industrial use of hiL~h frequency currents
held in Leningrad.
surface hardening of gears by induction heatin::- with two
frequencies. The method ensures heating along the contour
of gears with moduli of 3.5 to 5. During heating with a
lower frequency (1000 to 2000 c.p.s.),the bottom, of the
tooth gap is heated intensively, whilst at radio frequency
(300 000 c.P.s.) the tip of the tooth is heated. The
same inductor is used for both frequencies. The heatin-
with the lower frequency lasts 2.5 to 4 sees; ~herebythe
specific power consumption is 1.5 to 1.7 kW/cm . Heating
with the higher frequency is effected for q-5 to 0.7 see
using a specific power of 1.1 to 1.2 k.W/cml~. The
1000 c.p.s. current is generated by a 500 kW rotary
generator, whilst the 300 kc/sec current is generated
with an oscillator circuit of 400 kVI rating. During
hardening of gears made of steel 1145" cracks occur and,
therefore, the carbon content was reduced and alloy steels
36 r2C, 35cr etc. are being used. For fracturing a
tool of a surface hardened gear a force of 9.5 to 17 tons
is required, whilst the force required for fracturinG case
hardened gears after hardening,made of the steel 18xrT,
Card 7/lL4id not exceed 10 tons per tooth. Gears produced by using

129-4-12/12
All-Union Conference on industrial use of hiGh frequency currents
held in Leningrad.
two-frequency hardening wore dorim three times faster than
gears produced according to the old technology. Therefore,
in the further tests the steels 65r, 5oxr, 40XH and 4OXHKA
were used.
The paper of N. M. Rodigin, Ural Branch of the Ac.Sc. USSR
(Urallskiy Filial AN SSSR) was devoted to the new method of
induction heating of steel strip. The novel feature
consists in the fact that the electro-magnetic field
produced by an alternatin- current is directed perpendicular
to its surface and not in the longitudinal dir.---ction of the
strip. This enables using economical sources of current of
elevated frequency, namely, rotary generators. The required
temperature distribution alonG the width of the strip is
ensured by an appropriate configuration of the maLnetic
path and by an air gap between the poles. This method can
be used for annealing cold rolled strip, for heating and
for preheating of strip during rolling, pickling,
deposition of coatings, etc.
V. N. Bogdanov and V. A. Peysakhovich reported on the
practical application ofthe above method for annealing
Card 8/14 thin strip in the Leningrad Steel Rolling Mill (LeninGQradskiy

129-L[-12112
~11-Union Conference on industrial use of hi&,Ii frequency currents
held in Leningrad.
Staleprokatniy Zavod). The optimum, frequency depends on
the thickness and the width of the strip. For a lhiclmess
of 0.2 to 0.6 mm and a width of 100 mm it is recommended
to use a current of 8000 c.p.s.; for strip of 200 mm a
current of 2500 c.p.s. and for a width of 420 mm a current
of 1000 c.p.s. On heating strip to 700-900 C, the
uniformity of0the temperature along the breadth of the
strip is + 25 C. For heatinG,a two-turn inductor was
used, wheFeby the conductors of the current and of the
magnetic flux were water cooled. This method was applied
in the case of bright annealing of cold rolled strip.
For a speed of movement of the strip of 25 m/min the
required power was 200 M (for a frequency of 2500 C.P.S.).
The productivity of the equipment equalled 1 'Uon/hr. The
specific power consumption during induction heating is
180-190 kWh/ton. Compared with annealing in chamber
furnaces, this method has a number of advantages since
thereby the productivity per m of production space
is increased two to threefold, the annealing time is
reduced by several hundred times, uniform mechanical
Card 9/14 properties are ensured along the entire length of the

129-4-12/12
All-Union Conference on industrial use of high frequency currents
held in Leningrad.
strip coil and welding together of the strip during
annealing is prevented. The specific consumption of
electricity is higher for induction heating than for
electrical furnaces.
V. N. Gridnev, Doctor of Technical Sciences, Kiyev
Polytechnical Institute (Kiyevskiy Polite Idiniche skiy
Institut) dealt with the influence of the speed of
heating on the structure and the properties of steel.
Apparatus was built for the investigations which enabled
simultaneous recording of several physical parameters
.so that the following could be oscillosraphically recorded:
temperature, change in the length of the specimen and in
its electric resistance and also current intensity in
the inductor. 0The recording was effected with a speed
of 50 to 10 000 C/sec and the d~latometric curves were
recopded with a speed of 60 000 C/sec. The following
binary alloys were investigated - Fe-Cr (up to 8016);
Fe-Si (up to 3%); Fe-Ti; Fe-W; the C content was about
0.02%. Stee3scontaining 0.1; 0.45; 0.54; 0.77 and
1.12106 C were also investigated. The author has established
Card 10/14 that during heating of annealed carbon-free alloys, the

129-4-12/12
All-Union Conference on industrial use of high frequency currents
held in Leningrad.
transformation temperature does not depend on the speed
of heating and the magnitude of the volume effects
depends on the composition of the alloy and the preceding
heat treatment. When heating annealed iron-carbon alloys,
the transformation temperature is determined by the speed
of heating and by the initial structure. On heating
hardened low alloy carbon-free alloys, the transformation
temperature compared to that in the alloys in the annealed
statedQesnot change at all in some cases (Fe-S~; Fe-Ti),
whilst in other cases it decreases by 30 to L~O 0 (Fe-Cr
and Fe-W). On heating hardened steels, the dilatometric
recordings show clearly the volume changes caused by the
marten'site decomposition and by the phase transformation;
the decomposition cannot 0be suppressed not even at
heating speeds of 60 000 C/sec. At high heating speeds
of hardened steelsiothe.phase transformation takes place
in the range of 700 C, i.e. at lower temperatures than
the transformation during slow heating. Investigations
of the influence of the heating speed on the structure
and properties of hardened, carbon and alloy steels in
Card 11/14the case of electric temperinc,: shoi,~10 that at elevated.
,
A
~5

129-4-12/12
All-Union Conference on industrial use of high frequency currents
held in Leningrad.
heating speeds a favourable combination can be obtained
of the strength and ductility and also an increased
resistance to wear which is of practical interest.
In their paper I. N. Kidin, Doctor of Technical Sciences,
and Yu. A. Bashnin, Moscow Institute of Steel
(bloskovskiy Institut Stali) expressed the view that the
higher the heating speed the larger will be the
temperature range in which phase transformations will
take place. Experimental data show that pearlite-
austenite transformations proceed in the range of higher
temperatures. In the case of high frequency hardening,
higher temperatures are required than in the case of
heating in an ordinary furnace. This is attributed to
the fact that the phase transformations proceed with a
higher speed due to the more rapid rise in the temperature
and due to the sharp acceleration of the dissociation of
carbides and the diffusion of carbon in the ferrite. The
authors showed that it is justified to introduce a new
thermal parameter, namely, the speed of induction heating
in the range of phase transformations. This would enable
Card 12/14 the plotting of diagrams of preferential and permissible

129-4-12/12
All-Union Conference on industrial use of hih frequency currents
held in Leningrad.
hardening regimes which would conserve the character of
generally valid relations under conditions which are
reproduceable in normal production.
V. P. Pleshachkova (TsNIITMASh) read an interestinG paper
on the deformation of surface hardened steel. H.F.surface
hardening permits reducing the deformation of the steel.
The author investigated the influence on the deformation
OF the following factors: heating temperature, cooling
0
speed depth of the hardened layer, structure of the
starting material and also of the temperature and time
of heating in the case of low temperature tempering.
The results have shown that in the case of h.f. surface
hardening of rin specimens with small height to diameter
ratios (1:4; 1:75 produced from various steels, the
deformation manifests itself in a decrease of the outside
diameter and an increase in the height and in the inner
diameter. An increase in the temperature ledds to an
increase in the deformation along the outside and inside
diameters and manifests itself less on the height of the
rings. The deformation of rings made of alloy steels
Card 13/14 is greater than for rings made of carbon steels under

129-4-12/12
All-Union Conference on industrial use of hiGh frequency currents
held in Leningrad.
equal conditions of heating and cooling. Cooling in a
30 to 35% solution of glycerine and a y1o solution of
potassium permanganate brings about a reduction in the
deformation and in the crack formation particularly
in the casS of alloy steels (40X, 4OXH3. Tempering at
140 to 200 C reduces the dimensions as compared to the
hardened state and thereby the changes in the dimensions
of the height and the internal diameter are compensated
but the changes of the external diameter are amplified.
Increase of the tempering temperature brings about an
increase of the deformation.
Representatives from Roumania and East Germany
participated in the Conference. The German delegate,
E. Trippmacher,reported on the designs of compact h.f.
transformers with built-in magnetic paths produced in
East Germany.
VOTE: This is a complete translation and not an abstr2Ct.
AVAILA T : Library of Congress.
Card 14/14

SOV/129-59-1-5/17
AUThORS: , LozinsEjkS~i Doctor of Technical Sciences and
~-~66`nova, I.S. Engineer
TITLE: Certain Relations Governing the Deformation of Technical
Iron Diring Cjclic Temperature Fluctuations (Nekotoryye
zakonomernosti deformatsii tekhnicheskop zheleza pri
tsikli--heskikh kolebaniyakh temperatury)
PERIODICAL: Metallovedeniye i Termicheskaya Obrabotka Metallov,
1959$ Nr 1, pp 15 - 19 + 4 plates (USSR)
ABSTRACT: Investigations bj the authors of the relations governing
the deformation of commercial iron (0.0301o C) under
tension and presence of 3L temperature gradient in the
longitudinal direction of the specimen revealed that a
"super-high plastL~ity takz~s place" which is characterised
by the formation of two necks on the spealmen and by the
op.~-arrence of a --,ap4d sliding deformation. Prior to the
experimend+,s, the ape--imens were annealed for two hours
at 1 000 0 in vacuum. During the experiments., the
Opt-,U.1j"V"8 were heated bj passing through them 'a lcw-
voltage AC9so that a temperature gradient was produced
-in these specimens with a peak temperature at the centre.
The temperature distribution in the specimen is graphed
Cardl/4 in Figure 1 for peak heating temperatures of 800 and

SOV/129--59--i-,5/17
Certain Relationg Governing -rhe Deformation of Te--hAn-ical Iron
During Cyclic Temperature Fluctuations
WOO 0C, respeative-lyi in each specimen, a range ol
temperatures was generated, varying from about 400 "'C
at the edges and 1 000 C in the centre. The character-
isti.-Z of the cyclic change of the specimen temperature
is S-raphed in Figure 2; each cycle was 0; 60 see
duration and consisted of heating to 800 C and holding
it for Q2 se~; at that, temperature, then heating it to
1 000 C and again holding it for 2 see at that
liemperature, followed by cooling to 800 . C. In Figure 4
(plate),, 8 mi-rophotographs are reproduced of the surface
of the centrai zone of the iron during the tensile tests
and during isothermal holding at 1 000 C. In Figure 5,
10 microphc to graphs are :reproduced cf the szLrface of the
central zone of the specimen duxing tensile -tests
1)
(or = 0. 33 kg~mm and cyclic, temperature fluctuations of
800 ~T .1 000 C . In Figure 6, microphotographs are
reproduced cf the surface of the neck zone during cyclic
temperature fluctuations. In Figure 8. photographs are
reproduced of the specimens prior to tl~e tests and after
Oard2/4 'trarious test cycles. The deformation of the central

SOV/129--59-1-5/17
bertain Relations Governing the Deformation of Technical Iron
During Cyclic Temperature Fluctuations
zone of the neck during tensile stresses and cySlic
temperature fluctuations between 800 and 1 000 C in
the central., graphed in Figure 7. In Figure 9,
the depende&,PO1A,-4.-e change in th-e distance between
the centre of the neck and the edge on the maximum
temperature in the centre during cyclic tests.
The following conclusions are arrived at: 1) under
certain conditions of cyclic heating and cooling, a sharp
dearease in the resistance to deformation in tensile
loading is observed whioh leads to the formation of two
necks; the two necks a~e located in zones with the
temperatures?20t; 850 C; 2) appearance of failure
fcci in sections with a temperature lower than in the
midd'--- part of the specimen is attributed to the influence
of non-uniform distribution of carbon inside the grain
and alse -to the carbon concentration outside the
bo,mdaries of the grains and the blocks. In the case of
looal heating and nooling of individual zones in the
specimen up to the temperatures of polymorphous Mt4y
Card3/4 transformatLon, the proceeding reconstruction of the

SOV/129--59--i-5/17
Certain Relations Governing the Deformation of Technical Iron
During Cyclic Temperature Fluctuations
crystal lattice disturbs the coherent bonds of the atoms
and thi3 will result in a sharp drop in the resistance
to deformation only in those parts of the Uain whi3h are
enriche6 with -,,,arbon; 3) if the holding time at the
limit temperature values is increased, this detected
phenomencn is no longer observed. There are 9 figures
and 6 references, 4 of which are Soviet, 1 Czech and
1 German.
ASSOCIATION:
Institut mashinovedeniYa AN SSSR (Institute of
Me,~thaniaal Engineering of the Ac.Se.USSR)
Card 4/4

SOV/180-59-1-112/29
AUTHORS: Lozinskiy2 M.G., and Fedorovskiy, A.Ye. (Moscow)
TITLE: Influence of Vanadium, Tun asten, Chromium and Molybdenum
on the Internal Friction and Rate of Ageing of Technical
Iron (Vliyaniye vanadiya, vollframag khroma I molibdena
na vnutrenneye treniye I skorost' stareniya
tekhnicheskogo zheleza)
PERIODICAL: Izvestiya Akademii Nauk SSSR, Otdeleniye tekhnicheskikh
nauk) Metallurgiya I toplivo7 1959, Nr 1., pp 64--70 (USSR)
ABSTRACT: The authors have previously shown (Ref 1) that alloying
elements have an important effect on the value of the
internal-friction peak due to the presence of intruded
atoms in the alpha-iron lattice. They now describe a now
series of experiments to elucidate the nature and.
mechanism of this effect by measurement of the int.ernal
friction of technical iron alloyed with various quantities
of vanadium~ tungsten, chromium and molybdenum. The
alloys were melted in a 50 kg Induction furnace and
subjected to two-hour annealing. The alloys were hot-
forged into 12 mm diameter rsds, from which test pieces
Card 8t 0.01 mm in diameter and 12.'00 mm long were prepared for
internal friction maasu~~ements by grinding. The

SCV/18C -59-1-12/29
Influence of Vanadium, Tungsten, Chromium and Molybdenum on the
Internal Friction and Rate of Ageing of Techni;ial Iron
measurements were carried out on a type IMASh-6
installation with resonan--e-freqaency banding osoilla-
tions of a freely-suspended test pierce as previously
described by the authors (Refs 1_3). L find the
influence of alloying elements on the rate of ageing test
pieces wera wattex-quemhed after heating at 6800C for
30 minutes,. the rate being evaluated from the change in
the height of '--he internal-fTiction peak -with respect to
ageing time. All ageing test pieces were subjected to
isothermal heating at ll~ t 2.500. The results are shown
in Figs It and .~5 as internal. friction versus temperature
curves for vatious cl-ompositions of Fe-V and Fe-W alloys,
respecti~iely, and in Fig 6 for Fe + 4% Mo in the annealed
and hardened states. The dependence of the internal-
fr_iction paak values on ageing time (minutes) at 1150C
is sh,_;wn in Fig 117. The microstructures of the specimens
are shown in Figs 1--3. F:~-,m discussions of their own and
published results the a-uthors conclude that. although a
final d6:!ision on the me--hanism of the effe!.--ts of vanadium
Card p/1+ and chr,_.inium on the rata of ageing is not yet possible, it
appears that ir- soxe hardening fails to fix

sov/180-59-1-12/29
Influence of Vanadium, Tungsten~ Chromium and Molybdenum on the
Internal Friction and Rate of Ageing of Technical Iron
the state of solid solution with intruded atoms. Since
tungsten additions to technical iron accelerate solid
solution decomposition in the second stage and shorten the
first stage of ageing they must increase the mobility of
intruded atoms in alpha-iron, representing a decrease in
their diffusion activation-energy. Chromium has the
opposite effect and also smooths out the transition from
the second to the third stages. Both elements increase
the solubility of nitrogen and carbon in the alpha-iron
lattice. On the effect of the elements on internal
friction the authors suggest that the influence of
vanadium is mainly due to its combination with nitrogen
atoms but state that no estimate can yet be given of the
vanadium concentration necessary to eliminate the peak.
The effect of.tungsten is less than that of vanadium and
is explained iii~"inly in terms of grain size and the state
of precipitation of impurities. It had been shown
Card 3/)+ previously by the authors (Ref 1) that molybdenum in
concentrations of about 2% has little effect on the

SOV/180 -59-1-12/29
Influence of Vanadium~ Tungsten? Chromium and Molybdenum on the
Internal Friction and Rate of Ageing of Teohnical Iron
internal friction peak; with the 4 and 12% Mo alloys
now used complex effeots were obtained which the authors
discuss in terms of intruded--atom mobility.
Card i+/i+ There are 7 figures, 1 table and 9 references, 6 of
which are Soviet and 3 English.
ASSOCIATION: Institut mashinovedeniya AN SSR (Machinery Institute
AS USSR)
SUBMITTED: Septembe.- 1, 1958

SOV/180-59-3-lo/43
AUTEORS: Lozinskiy, M.G. and Mirotvorskiy, V.S. (140scow)
TITLE, Some Rules for the Change in Micro-Hardness (.),C
Technical Iron on Heating ever a Wide Range of
Temperature and Extension in a Vacuum
.-H-.RIGDlCAL: Izvestiya Ahademi-i nauk SSSR, Otdeleniye tekhnicheskikh
nauk, Metallurgiya i toplivo, 1959, Nr 3, PP 52-61 (USSR)
A~jSTRACT; Theauthors developed the type DiASh.-9 testing machine
at the Institut mashinovedeniya (Machin;ry Institute)
AN SSSR (AS USSR) in 1956. it is intended for the
measurement of alloy micro-hardness in a vacuum at
temperatures from room to 1300*C with tensile stresses
up to 60 kg/MM2 and indentor loads of 2 to 50 g. The
construction of the machine is shown in Fig 1: the left
hand diagram shows the machine ready for selecting the
test spot or for measuring the indentation; the right
hand ready for indentation. The figure does not
include the indentor position-adjusting screws. A
general view is given in Fig 4 to 6 and the circuit :Ln
Fig 5- One face of the test piece (Fig 2) is polished;
its overall length is -10 mm. The indenter (Fig 3) is
Card 1/4 fitted t-rith a diamond or artificial sapphire tip, mm

sov/180-59-3-10/43
Some Rules for the Change in Micro-Hardness of Technical Iron on
Heating over a Wide Range of Temperature and Extension in a Vacuum
long and 3 mm in diameter. The diamond cannot be
useg with carbide-forming alloys and temperatures over
900 C. The indentation is photographed with a type
MFN-2 camera and measured with a type AM9-2 or
AM9-3 ocular micrometer. Heating is by direct passage
of an electric current and temperature is measured with
a thermo-couple welded to the middle part of the test
piece and a type EPD-12 electronic potentiometer.
Evacuation is effected by a type TsVL-100 oil-vapour
pump backed by a PVN-20 rotary pump, the vacuum being
measured with a type VIT-1 gauge. 10 to 20 indentations
were made per test piece which had before the test been
annealed in vacuum at 9500C (for I hour) to remove
surface work hardening produced by the polishing. As
an example the authors gave.the curve of micro-hardness
against temperature (Fig 7) obtained for technical iron
with indentor loads of 50 g applied for 15 see in a
residual pressure of 10-5 aim Hg. The curve shows a
steady fall from 0 to 200 and about 320 to 870. A
Card &A maximum occurs at about 300*C and there are smaller peaks

sov/180-59-3-lo/43
Some Rules for the Change in Micro-Hardness of Technical Iron on
Heating over a Wide Range of Temperature and Extension in a Vacuum
at 910 and 1020. Fig 8 shows corresponding photomicro-
graphs of the iron surface. Another series of
experiments was carried out to find the influence of
tensile stress on micro-hardness of iron at temperatures
up to 1000*C. Ten indentations were made at each of the
stresses chosen, at a given temperature separate
experiments being done at different temperatures. The
results (Fig 9) show that micro-hardness has a minimum
at definite stress values which decrease as the
temperature rises. The rise in micro-hardness at higher
stress values is considerable: the authors attribute
these increases to work hardening due to plastic
deformation. The authors hope to extend their work to
the influence of prolonged loading over a wide temperature
range on strength values as estimated fromoicro-hardness.
There are 9 figures and 10 references, 7 of which are
Soviet, 2 English and 1 German.
ASSOCIATION:Institut mashinovedeniya AN SSSR (Institute of blachine
r
3

67295
00
sov/180-59-4-32/48
AUTHORS. Lozinskiy, M.G. and Erlikh, L.B. (Moscow, Odessa)
TITLE: Magneto-Elastic Effect in Induction Heatingile
;q
PERIODICAL: Izvestiya Akademil nauk SSSR, Otdeleniye tekhnicheskikh
nauk, Metallurgiya i toplivo, 1959, Nr 4, pp 200-202 (USSR)
ABSTRACT: Usually, the effect of the stressed state on the
magnetic permeability is ignored in induction heating.
In reality, for most carbon steels in magnetic fxelds of
medium and high intensity, tension reduces the
permeability somewhat whilst compression substantially
increases the permeability. This effect would have little
significance in practice if a uniform stress existed
throughout the heated body (except for a variation in
the duration of heating). In fact, the stress
distribution is non-uniform. This causes a non-uniforni
distribution of temperature. An example is the well known
striped heating observed before the entire surface reaches
the Curie point temperature. The distance between the
stripes is known to be inversely proportional to the
square root of the frequency. A physical exp' 'i'anation of
this effect is given on the basis of the mag--eto-elastic
Card 1/2 effect and an approximate analysis yields the same formula

67295
sov/AO-59-4-32/48
Magneto-Elastic Effect in Induction Heating
previously obtained by observation. Basically, the
phenomenon is due to the formation of slight corrugations
in the compressed heated outer layer. Another result of
the magneto-elastic effect is the bright glow emitted by
the edges of the cylinder when the end faces and side
surfaces are still cold. It -is stated that the effect
shows promise as a method of experimental investigation
of the stressed state in the surface layer of machine
components. There are 2 figures and 6 Soviet references.
SUBMITTED: February 6, 1959
Card 2/2

SOV/129-59-5-8/17
AUTHORS: Dr.Tech.Sci. M.G. Lozinskiy,, and Engineer Ye.P Sincdova
TITLE: Investigation of the Temperature Dependence of the
Hardness of Iron-Molybdenum and Nickel-Molybdenum Kl`oys
(Issledovaniye temperatarnoy zavisimosti tverdost '1
zhelezomolibdenovyi-l-, i rikellmolibdenovykh splavov)
PERIODICAL: Metallovedeniye i Termicheskaya Obrabotka lletallov~
1959, Nr 5, pp 35-4~0 + 1 plate (USSR)
ABSTRACT: The results are described of investigations carried out.
in the Institute of Mechanical Engineering, Ac.Sc, USSR,
(Institut Mashinovedeniya AN SSSR) relating to the study
of iron-molybdenum and nickel-molybdemm alloys by means
of short-duration and long-duration hardness measurements.
The materials for the specimens were produced In a 50 kg
capacity induction furnace. The iron-base alloys
contained respectively 4% Mo (alloy 204) and 1.2% Mo
(alloy 212). The nickel-base alloys were alloyed
res ectively with 7% Mo (alloy 307) and 25% Mo (alloy
325Y As can be seen from the diagram (Fig 1) the alloys
204 Ld 30'7 remain in the entire temperature range single-
Card 115 phase alloys and do not become transformed. The alloys
212 and 325, which had higher molybdenum contents, aTe

BOV/129-59-5-8/17
Investigation of the Temperature Dependence of the Hardness of
Iron-Molybdenum and Nickel-Molybdenum Alloys
two-phase alloys in the state of equilibrium and after
quenching from the single-phase range they are prone to
dispersion hardening. The alloys 204 and 307 were
investigated after vacuum annealing at 9000C for two
hours followed by slow cooling in the furnace. The alloy
212 was investigated after quenching from 12000C in oil;
the alloy 325 was investigated after quenching in water
from 9000C. By means of hardness measurements, the
kinetics of ageing of the alloys 212 and 325 at various
temperatures were studied. The influence of ageing on
the microstructure of the alloy 212 can be followed from
the microphotos reproduced in Fig 2 (plate). The results
are described of the short-duration hardness measurements
at 20 to 10000C in vacuum for the alloys of the systems
Fe-Mo and. Ni-Ho (see graph, Fig 4). The duration of
applying the indentor in each case was one minute. Data
on the kinetics of ageing of experimental alloys in the
temperature range of 300 to 1000 OC are graphed in
Card 2/5 Figs 5 and 6. The temperature dependence of the "long-
duration" hardness, i.e. of the hardness values measured
"tV

SOV/129-59-5-8/17
Investigation of the Temperature Dependen,e of the Hardness of
Iron-Molybdenum and Nickel-Molybdenum Alloys
with load application times Of 30, 300 and -1000 seos ` aie
given and discussed. It is shown that a concentration 01:
the alloying element (molybdenum) which shifts the alloy
from the single-phase range to the two-phase range, b,_r-ings
about a hardening in the entire investigated. tempera tu.~%
range. In the range up to 7000C dispersion hardening
takes place in two-phase alloys, as a result of whic-14
there will be a sharp in-,~rease in the hardness.
Investigation of the long-duration hardness of nickel
alloys containing ? - 25% MO has shown that for the ageing
alloy 325 the hardness at 600 to 700 OC is higher than it
is at 5000C and the dJ.fferenf-,e between the values of the
hardness measured with indentation durations of 30 and
3000 sees (which characterises the tenden.c-y to creep of'
the material) is approximately the same at 500, 600 and
700 OC. An increase to 800 - 900 OC in the temperature
of testing long ... duration hardness of the alloy containing
25% Mo revealed that this alloy softens more int-insively
Card 3/5 than an alloy containing 7% Mo. At 1000 OC nickel--lbase
alloys showed the same degree of softening for various

SOV/129-59-5-8/17
Investigation of the Temperature Dependence of the Hardness of
Iron-Molybdenum and Nickel-Molybdenum Alloys
Mo contents and the character of the curve of the hardness
versus duration of applying the indentation load is
similar to that obtained in tests at 500 to 600 OC. The
elastic properties of the alloys, which are characterised
by the values of the modulus of elasticity, are little
influenced by an increase in the molybdenum content
(within the investigated limits) and with increasing test
temperature the modulus of elasticity decreases
monotically. The values of the logarithmic damping
decrement of oscillations (internal friction) did not
change in any of the investigated alloys up to 5000C,
However, on increasing the heating temperature further
Card 415 the damping intensified sharply; in single-phase alloys

SOV/129-59-5-8/17
Investigation of the Temperature Dependence of the Hardness --,f
Iron-Mol-ybdenum and Nickel-,Molybdenum Alloys
this process began at lower temperatures than in
two-phase alloys.
There are 8 figures and 5 Soviet references,
ASSOCIATION: Institut Mashinovedeniya AN SSSR (Institut-i of
Mechanical Engineering,, Ac. Se. USSR)
Card 5/5
VMS

.; ': .~ V
SOV/1.80-59-6-5/31
AUTHORS: 1ozinsk1Y1_KG.$ 6JM&=y_44,_jj.$ and Fadarpjaklyg A,Ye.
TITLE: On the Behaviour of Pure and aommorcial-Grade Ironl
during Deformation 4nder the Conditions of Cyclic
Temperature-fluctuations
PERIODICALs Izvestiya Akademii nauk S8SR,0tdeliiniy6 takhnicheskikh
nauk$ Metallurgiya i toplivol'.19%Nr 6: PP 24-36 (UqSR)
ABSTRACT: The object of the present inveatigationg carried. outlat
in n 4
the Institute of the n-4 MeahingA, Acflo. USSR; 'gas
to S~Ed_y the affect of cyalld on
the kinetics oT the deformation of commercial-gade iron
(containing 0.03% C) and high purity material containing
0.002% 0) stressed in tension with the view of deter-
mining the effect of small aljoy-j.ng add-itions on the
character of the deformation of specimens under these
conditions, Thwexperiment* were conducted in vacuum,
the tensile test pieces being heated by low voltage, h19144,
current repist~ance heating. The shape of the test pieces
of square 6ross-section aroa Q z 3 490 , with one of the
Card sides polished for metallographic examination, is
1/9 illustrated in Fig la, showing the flexible bars (details
2 and 3) supplying the power, terminal screws

67829
SOV/180-59-6-5/31
On the Behaviour of Pure and Commercial-Grade Iron during
Deformation under the Conditions of Cyclic Temperature Fluctuations
(details )+ and 5), and the swivel-type grips (details 6
and 7). Since a larger quantity of heat was conducted
away from the ends of the test pieces, and since their
cross-section area was larger than that of the gauge
length, a temperature gradient was set up in the test
pieces; this temperature gradient7 in specimens with the
maximum temperature of 800 and 1000 OC, is illustrated in
Fig 16, where the temperature (OC7 horizontal axis) is
tlotted against the distance (mm) from the centre of the VK
est piece. The temperature of the centre of the
specimen was made to fluctuate between 800 and 1000 OC.
The circuit diagram of the automatic temperature
controller and automatic recorder of the number of the
CYclic temperature changes is shown in Figs 2 and 3;
Fig 2 also shows the arrangement of the test piece in the
vacuum chamber and a.metallurgical microscope, mo;~nted
Card in the lid of the vacuum chambers and used to study-the
2/9 structural changes taking place in the test pieces
during the experiments. The first significant fact
observed was that "necking" of the commercial-grade iron

67829
SOV/180-59-6-5/31
On the Behaviour of Pure and Commercial-Grade Iron during
Deformation under the Conditions of Cyclic Temperature Fluctuations
specimens occurred not in the centre of the test piece,
but at two points situated symmetrically on both sides of
the "hot zone" (about 10 mm from the centre)7 where the
temperature fluctuated between 750 and 850 OC. (Two
necks were formed when the time at the lower and higher
temperatures did not exceed 60 see; when the test piece
was held at the temperature for longer periodsq only one
neck in the centre of the specimen of the test piece was
formed). This, apparently anomalous5 effect was
attributed to several factors. While the overall carbon
content of the investigated material was 0.03%, the local
carbon concentrationg particularly at the grain and block
boundaries, could be considerably higher. Bearing in
mind that the temperature of the a -4 y transformation
changes from 910 to.721 OC when the carbon content varies
from 0 to 0.83%, it will be seen that the C-rich, grain-
boundary regions in the central part of the tensile test
Card piece whose temperature fluctuated between 800 and 10000C
3/9 remained in the y-iron range throughout the experiment,
while in the interior of the grains (blocks), each

67829
SOV/180-59-6-5/31
On the Behaviour of Pure and C:ommercial- Grade Iron during
Deformation under.the Conditions of Cyclic Temperatu.re.Fluctuations
temperature fluctuation was accompanied,by-the a -4 T
(heating) or T'--4 m.(cooling) transformatibn. The
situationin~the parts of the specimens where the
temperature fluctuated between 750 and.A~E_OC, was quite
different; here, the interior of thelgrainb retained
their a-iron structure throughout the experiment, while
the grain-boundary regions were undergoing the a -~ Y
.4 a transformations.. The. strength.of the
and Y,-
T-phdse-" is -considerably higher than that, of the
and this..fact accouXits..for the high resistance.to,
deformation of.,the-contral (hot) part ofAhe test pieces
where the grain boundaries retained the.ir.'T-phase
structure throughout, the duration of e~:ch-..tdst,,.
Regarding ~he.r4gioAs*,of "critical" temperatures, where
Card necking occurred~~it should be 3~emembered-that the
4/9 mechanical,propdrties of iron are' adversky dffected by
.the .; Y. trahst6ftation which is,-adcompanied by a
partial la5s of th6t6ohdreU bond between.'the atoms and
by volumetric changti-;which set up inteinal.s.tresses in
the microvolumes ofihe material underg'b" the

67829
SOV/180-59%6*-5/31
On the Behaviour of Purb,andlCoiamercial-Grade Irboa-:dftring
Deformation under,the Conditioxw,qf Cyclic ,Tempe~aturo F1,4etuations
..trans f0ination;. i .t'Vii for this ieason''-that. .applied
stresses*as low as 0,33-0-~5 kg/mmP- we~b.sufficie'nt to
cause deformation (pecking) in those parts of the test
piece ii~ which tho'ca'rbon-rich grain Voundaries were
contimously.undergoirig. the c~.;g,?,y,- . tranq formation.
This viq)w.'was cohfir~(ed.by the fqlat--that ir *
q hen specimens
of high purity'4ironFVer'e tested under -the 'same
condition, one nbck,oxxily was formed in"the'..c6ntre of the
test Oiece, (the-. table- *on p 28 gives the che*mical~ analysis
.o'f the commercial 8rade (top iine) -and -high puri.ty'
.(bottom line) experimental materials).:.~The proc6ss of
def6rit' ti -of ~omm6r~ b'j'ected-to cyclic
a on ial-griae iron, -su ; -
temperature fluctuations between'.750 and 950,9C ..(the time
taken%to heat the ~Pdt piebe.fiom the loweir-to t#e upper
limit, of,t6mperdtixre-being 10 .sea', and.the* time'at the
temperatilre '2-sec),'while under- .an appl. .ied--~ensile stress
of -0.33. k,
g/mia2;,-is;-.ilj4strated iri. F~ig -.lower
Card our-ie *shows the'Varil&fi6n of "the -te'mpe a ur .e ..(00 right-
5/9 hand scale) and the'upp6r curve the'variatio'n6f
Slongation (el left-hand scale) with time (see).
A.
A
4

67829
sov/18o-59-6-5/31
On the Behaviour of Pure and Commercial-Grade iron during
Deformation under the Conditions of Cyclic Temperature Fluctuations
It will be seen that an anomalous increase in the length
of the test pieces was observed during cooling through
the 800-730 OC temperature range, and that the rate of
deformation during heating was highest in the same
temperature range. The structural changes occurring in
commercial grade iron during the experiments are illus-
trated by a series of microphotographs (X 201+)q
reproduced in Fig 6t and showing the appearance of the
polished surface of the specimen in the region of et~
necking; the temperature of this region fluctuated
between 750 and 850 OC the duration of the heating and
cooling cycles being 26 and 2-2 see, respectively7 and the
time at the temperature, 2 sees the test piece was under
a tensile stress of 0.55 kg/mm2.' Fig 6a shows the
surface of the test piece before the test; the direction
of the applied stress is shown by arrows; the
impressions~ made by the diamond pyramid used in micro-
Card hardness tests, assisted in assessing the magnitude and
6/9 character of the localized deformation taking place
during the experiments. Fig 615 shows the surface of the

6"7829
sov/18o,.59-6-5/31
On the Behaviour of Pure and Commercial-Grade Iron during
Deformation under the Conditions of Cyclic Temperature Fluctuations
test piece after 5 min at 1000 00; faint outlines of the
grain boundaries-of the a-phase are visible. Figs 66 -
VK show the surface of the test piece after 5, 10t 20 and
50 heating/cooling cyclesq respectively, and attention is
drawn to the formation of cracks in the regions. indicated
by arrows in Figs 6Z and e. The course of deformation
of high purity irong tested under the same conditions as
the commercial grade material (except for the stress
which2 in this case was 0.05 kg/mm;-')g is illustrated by
the microphotographs reproduced in Fig 7, which show the
surface of the central (necking) part of the test piece,
the temperature of which fluctuated between 800 and
1000 OG. Fig 7a shows the surface of the test piece
before the experiments; the appearance of the same
surface area, after 5 min at 1000 OC, and after 5, 102 20
and 50 heating/cooling cycles is illustrated by the
subsequent micrographss the increasing degree of
Card fragmentation of the grains with increasing number of the
7/9 temperature fluctuations should be noted. The difference
in the behaviour of the investigated materials is also

67829
SOV/180-59-6-5/31
On the Behaviour of Pure and Commercial-Grade Iron during
Deformation under the Conditions of Cyclic Temperature Fluctuations
illustrated by the graph reproduced in Fig 81 where the
elongation of the test piece (e. %) is plotted against
the number,, n, of the temperature fluctuations for the
commercial grade iron extended under 0.55 kg/mm2
(curve 1) and high purity iron extended under 0.05 kg/mm2
(curve 2), It will be seen that after 50 cycles, the
total elongation of the high purity and commercial grade
iron was 13 and 38%, respectively, although the stress
applied in the latter wase was eleven times higher than
that in the formir, Another interesting fact observed
by the present authors was the formation and growth of
conically shaped protrusions an the surface of high
purity iron in the central (hottest) part of the test
pieces. The appearance of the commercial grade and high
purity iron test pieces.after 150 temperature fluctua-
tions (800-1000 00 is shown in Figs 9a and 96,
Card respectively (the arrows showing the necking zones); the
8/9 necking zone of the test piece shown in Fig,96 is shown
at a higher magnification (X 7). in Fig-90. The conical
protrusions formed on the high purity iron after

67829
SOV/180-59-6-5/31
On the Behaviour of Pare and Commercial-Grade Iron during
Deformation under the Gonditions of Cyclic Temperature Fluctuations
200 temperature fluctuations are shown in Fig 10a (X 22);
microphotographs (X 100 and X 200) of the conical
protrusion, marked k in Fig 10, are reproduced in
Figs 106 and 0,,,respectively, and show clearly the
Polyarystalline character of these growths whose
formation had also been observed by Ciziron and Lacombe ~'r
(Ref 10), although these workers considered them to be
polygonized--single crystals. The experimental results
reported in the predent paper prove that small alloying
additions markedly'improve the strength of.iron strained
under the conditions of cyclic temperature variations.
,They show~,.also,'-.that an increase in the alloying
L
additions content l6wers considerably the temperature of
the minimum strength
-Card There are 10 figures, 1 table and 10 references~ of which
9/9 )+ are Soviet, 4 English, 1 French and 1 Czechoslovak.
SUBMITTED% July 17, 1959 J.

KHRUSHCHOV, Mikhail Mildwylovich; BERKOVICH, Yefim Solomonovich;
LOZINMIT,.*.G.,.doktor tekhn.nauk, otv.red.,- KOVALISLAYA,
I.F.. takhn.red.
[Studying the hardness of ice) Izuchenie tverdosti 11da.
Moskva, Izd-vo Akad.nauk SSBR, 1960. 48 p. (MIn 13:7)
(Ice-Testing) (Hardness)

LOZVSKV~' Mikhail Grigorlyevich
High temperature netallography. Ne,
Pergar-on Press, 1961 jUS., diagrs-, grarihs,
,+14 D. i1
xix, '- .
Translated from tile original 11"s'"'
turnaya metallografiya, MOSCOW-1 1956.
Bibliography! P- 4r&j -1,72.
London,
Yrk9
nort., tables.
Vysokotempera-

1.1100
26242-
S./122/61/000/001/009/015
A161/A130
AUTHOR. Lozinskiy, M.G., Doctor of Teohnioall Sciences
TITLE. New methods for increasing the atrength of steels and alloys
used in various.machine industry branches
PERIODICAL- Vestaik masblnostroyeniya, no. 1,.196:L, 56 - 64
TEXT: The article presents a brief general discussion of the latest
development tren&s with references to non-Soviet publica:1.ions and concerning
whiskers, improved hardening technique (Ref. 4-. E. M. H. Lips and H. Van Zuilen,
"Metal Progress" v. 66, no. 2, 1954), %uzforming" developed &t the Ferd Works,
"termomagnadynamtx" of RDCA, and data obtained with the Sovist TMO Itermomekha-
nicheskaya obrabotka (thermo-meohanioal treatmant)j. TMO if under-develoiPment,
and the author taken part in the work. It had been dis-ouaasd in Ref. 12 (So-
kolov,.Ye. N., M. G. Lozinskiy, Ye, I. Antipova, Strnakt.ur& granits zeren i zha-
roproohnost' stali 6oiMm8B, HMetallovedentye i obrabotka metallov", no. 11,
10) and specified in Author's Certificate No. 12394 c~la`es 180' 139' granted
Lozinskiy, M.G. and Sokolov, Ye. N. (Ref. At "Byu,llleten' lzobr,~tsniy no. 21,
1959). Its essence is combination of plastic. deformtIon I'lo 25 --35 % (induced
Card A

26242
S/122/61/000/001/009/015
New methods for increasing the strength .... A16.,/Ai3o
after homogenization of T-solid solutifar at 1,2000C and subsequent cooling
down to 1,100 - ;0000) with immediate cooling which prevents reerystalization
and fixes a specific structure caused by defor7iation. Aging completes the
treatment. TVIO raises the long-term durabiltiy of austenitia steel and alloys
in tests with heating, provided the recrystallization temperature is not exceed-
ed. The strengthening effect works in auatenitic steel up to 900 9500C. The
specific structure produced has *serrated" grain boundar-ie.R with 5 10 Micron
protrusions. Besides, grains are split into pi6ces and the size of the mosaic
blocks reduced. The result of the treatment not properly conducted may be the
start of reorystallization and formation of fine chains of new grain in the
place of the"serrations". The formation of the new grains on the boundaries
destroyed the strengthening effect of TMO, but properly done TMO rgsulted in
4 - 5 times longer time to rupture in -tests at 9000C with 14 kg/m tension
stress in comparison to results after usual standard quenching with aging.
TMO can be used in basically five '_ combinations with plastic deformation (Figure
9): a - rolling hot blank (3) in rolls (1,2) with several. metersa minute into
intensely cold zone (4), e.g., a quenching sprayer; b - drawing; a roll forg-
ing; d-stamping (where TMO is complicated), and e - extrusion. The layer of
Card 2/4

26242
S/122/61/000/001/00~/qI5
New methods for increasing the strength .... A161/A13O
specific kcrostructure is 4 mm deep, and metdl of 10-15 mm is pen6trated.
but in large metal pieces the heat conduction can cause recrystallization and
this must'be considered. The method is good for looal strengthening. A device
for this purpose is sohqmatic~lly illustrated (Figure.10). There are 10 figures
and 14 references: 4 Soviet-bloc and 10 non.;-Soviet-bloc. The latest date refer-
ences to the Llnglish-language publications read as follows: Schmetz, D. R.,
Shyne J. C., Zackay V. F., Austenitio "cold working" for ultra high strength.
"'Metal,Progress, v. 76, no.1959; Are 1 Million psi,Steels Possible? "Steel'tI
v.145, no. 17, 1959; McGuire F. G., Breakthrough on heat treating promises huge
gains on strength", "Missilqs, and Rockets", Sept. 28, 1959; Magnetic Quenching,
"Metal Treatment and.Drop Forging", v. 27, no. 180, 1960.
ASSOCIATION: Institut mashinovedeniya AN SSSR (Institute of Science of Ma-_
chines)
card 3A

E02l/E4o6
Z. (MOSCOW)
AUTHORS: -Lozinskiy, 1M.G. and Pertsovskiy, N
TITLE: Kinetics and Mechanism of Deformation of Metals at
High Temperatures and Different Sjrain Rates
PERIODICAL: Izvestiya Akad nauk SSSR, Otdcleniye tekhnicheskikh
nauk, Metallurgiya i toplivo, 1961, No.1, pp.96-107
TEXT:* Direct observation by microscope or taking of photos of
changes in the microstructure of metals and alloys during testing
in a wide ran Ae of temperatures was not possible until 1960, when
a new machine WMAul -5c (IMASh-56) was designed by the present
~--authors and constructed'at the Institut mashinjovedeniya AN SSSR
(Instilute of aciRnce--of Machines AS USSR). The technical
characteristics of the new machine -f re described and results
obtained on the machine on nickel'6re given. The machine enables
tests to be carried out in a vacuum up to 1200'C with a controlled
strain*rate. Indentations are made on the surface of the
specimens, with a diamond pyramid to ensure that examination of the
same part is carried out each time. Microphotographs of the
surface are taken at various intervals during testing. The
elongation of the specimen is measured to + 0.005 mm. The machine
Card 1/ 1.6

s/lBo/61/ooo/ool/007/015
Kinetics and Mechanism of ... E021/E4o6.
was used to study the effect of temperature and rate of deformation
on samples of commercially pure nickel (99.85% Ni with 0.02 C.,
o.o6 si, 0.03 Cu, 0.005 S and 0.0020,0' P). Specimens were
heated at 11500C for 3 hours to give a mean 2grain diameter of 0.15
to 0.18 inin and a hardness of 65 to 70 kg/mm . The samples were
tested at 600 and 10000C with strain rates of 0.5 and 2.8 x 102mm/h.
The results are shown in Fig.4. A decrease in rate of deformation
results in a mariced decrease in the strengthening effect occurring
during plastic deformation at a given temperature. Specimens
tested at 2.8 x 102 mm/hour at both temperatures fractured after a
large degree of deformation with a transcrystalline fracture and
formation of necking. Specimens tested at 0.5 mm/hour and 10000C
gave a ductile fracture with preliminary formation of necking in
spite of the fact that many intercrystalline cracks appeared in the
process of deformation. At 0.5 mm/hour rate and 6000C, brittle
fracture occurred without any substantial local deformation.
Fig-5- 8 show series of micropbotographs taken during testing. An
increase in 'the rate of deformation from 0.5 to 2.8 x 102 mm/hour
at 6000C results in intensification of the processes of slip in the
grains as shown by the slip lines. Increasing the rate from 0.5 to
Card. 2/ 16..
-,Z:

S/180/61/000/001/007/015,
ROWE06
Kinetics and Mechanism of ...
2.8 x 102 mm/hour at lOOO*C results in a change in the mechanism of
deformation. With a rate of 2.8 x 102 mm/hour, intensive slip
A.
..first oc'curs and with greater deformation recrystallization occurs.
At 0.5 mm/hour, no slip lines are seen, migration of grain
boundaries occurs, a substructure is formed and intercrystalline
cracks are seen. There are 8'figures, 2 tables and 17 references:.
10 Soviet and 7 non-So,~iet.
ASSOCIATION: Institut mashinovedeniya AN SSSR.
(Institute of Science of Machines AS USSR).
SUBMITTED: July 211 1960

S/129/61/000/002/013/014
E073/E335
AUTHOR. Lozinskiy, M.G., Doctor of Technical Sciences
TITLE: All-Union Scientific-technical Conference on
Applying Induction Heating in the Heat-treatment
of Metals
PERIODICAL: Metallovedeniye i termicheskaya obrabotka
metallov, 1961, No. 2, PP..59 - 61
TEXT: The conference was convened by the Gosudarstvennyy
Komitet Soveta Ministrov SSSR po avtomatizatsil i washino-
stroyeniyu (State Committee of the Council of Ministers, USSR,
on Automation and Machine-building), Gosudarstvennyy nauchno-
tekhnicheskiy komitet Soveta Ministrov SSSR (State Scientific-
technical Committee of the Council of Ministers of the USSR)
and the Metals and Heat-treatment Section of the Scientific-
technical Society of the Engineering industry.
It was held on Octftr 28, 1960 in Moscow. 22 papers and
10 communications were read and discussed and there were
378 participants.
Card 1/3
Lai
N, Pin-,

S/129/61/000/002/013/014
E073/E335
All-Union Scientific-technical Conference on Applying
Induction Heating in the Heat-treatment of Metals
Of the papers read, the following are specifically mentioned
and summaries of their contents are givent
Doctor of Technical Sciences, Professor I.N. Kidin (Moskovskiy
institut stali (Moscow Steel Institute) "The Importance of
Electrothermal treatment in Modern Metals Technologyii.
Candidate of Technical Sciences N.P. Glukhanov (NII TVCh im.
V.P. Vologdin) "State and ProSpe'cts of Industrial'Application
of High-frequency Currents".
Candidate of Technical Sciences Yu.M. Bogatyrev (TsNIITMASh)
"Through Electrothermal Treatment of Steel".
Candidate of Technical Sciences K.Z. Shepelyakovskiy
(Moskovskiy avtomobillnyy zavod - Moscow Automobile Works)
"Surface-hardening of Steel After Deep Heating".
Candidate of Technical Sciences M.N. Bodyako (Fiziko-
tekhnicheskiy institut AN BSSR - Physicotechnical Institute
AS BSSR) "On Recrystallisation Phenomena During Induction
Heating".
Card 2/5

S/129/61/000/002/0131014
E073/E335
All-Union Scientific-technical Conference on Applying
Induction Heating in the Heat-treatment of Metals
Candidate of Technical Sciences M.N. Klimochkin (TsNIITMASh)
"Surface Electric Hardening of Spheroidal Cast Iron".
I.S. Demchuk and G.N. Ivanov "Flow-production by Mechanised
Bending and Quenching of Rolled Sections Using High-frequency
Heating".
Doctor of Technical Sciences M.G. Lozinskiy (Institut
mashinovedeniya AN SSSR - Machinery Institute of the AS USSR)
"Trends in the Development of Instrument Manufacture and of
Equipment in the USSR and Abroad for Induction-hardening of
Steel and Cast Iron".
Doctor of Technical
frequency Equipment
Improving Them".
A.A. Terzyan (Armya:askiy
VNIIEM) "New Series
125 kW'',
Card 3/5
Sciences Professor A.V. Donskoy "High-
With Tube Oscillators and Methods of
filial VNIIEM Armenian Branch of
of Rotary Frequency Converters 12 to

s/i2g/61/000/002/013/014
E073/E335
All-Union Scientific-technical Conference on Applying
Induction Heating in the Heat-treatment of Metals
V.F. Artemlyev (Uralmashzavod) and I.M. Likhtshteyn
(VI>TITyazhmash) "Equipment for Quenching Large Components of
Machines After High-frequency Induction Heating".
1.P. Russinkovskiy (ENIMS) "Application of Ferrites for
Intensifying the Process of Induction Heating".
Candidate of Technical Sciences K.Z. Shepelyakovskiy and
1.N. Shklyarov (Moscow Automobile Works) "Automation of the
Process of Heat-treatment of Components Using High-frequency
Heating".
Doctor of Technical Sciences Professor I.N. Kidin and
Yu.G. Andreyev (Moscow Steel Institute) spoke of a new method
of nitro case-hardening of steel.
S.Ya. Yaitskov (Moscow Automobile Works) spoke of a method
of intensifying induction through-heating of blanks for
forging.
Card 4/5
T

S/129/61/000/002/013/014
E073/E335
All-Union Scientific-technical Conference on Applying
Induction Heating in the Heat-treatment of Metals
YO.I. Natanzon (Gorlkovskiy avtomobillnyy zavod - Gor'kiy
Automobile Works) spoke of improving the technology of
surface-hardening of mass-production components.
G.F. Golovin (NII TVCh im. V.P. Vologdin) spoke of the
cooling capacity of fluids in the case of feeding them as
sprays.
A resolution was passed relating to eliminating the
inadequacies of induction heating and its practical utilisation
in engineering, pointing out the extreme importance of wider
utilisation of induction heating from the point of view of
reaching the targets set by the Seven-year Plan.
Card 5/5

SADOVSKIY, V.D.; SOFOLYOV, Ye.N.; L.O_ZIrISKIY, M.G.; PELIOVA, S.N.;
ANTIPWA, Ye.l.; GAYDUKOV, M.G.; MIRYIELIS11TErv), V.A.
Effect of hot working on the heat-re-sistant properties of austenitic
steel. Issl. po zhar,)pr. splav. 7:202-209 '61. (YIIHA 14:11)
(Steel alloys--Thermal properties) (Rolling (I'letalwork))

26576
s/l2q/61/ooo/oo8/ooq/oi5
ig 8z" lo4jr ~ng E073/E335
AUTHORS: _j:jozinskiy, M.G., Doctor of technical Sciences,
Zusmanovich, G.G. and Mirotvorskiy, V.S., Engineers
TITLE: Dependence of the Microhardness of Wear-resistance
Coatings on Temperature
PERIODICAL: Metallovedeniye i termicheskaya obrabotka inetallov,
1961, No. 8, PP- 37 - 39
TEXr: For evaluating the performance of the -,;-ear-resistant
coatings, it is useful to determine 1.iieir microhardness at
elevated temperatures. A. Brenner (Ref. 1 - Journal of
Research, Nat. Bureau Standards, Vol 46, No. 2, 1951) published
results on microhardness tests at 60~ OC in an in-~:rt- gas
carried out on chromium-plating using loads of 30 - 20-D 9.
Apparatus was built in 1958 at Liia institute of -the authors
which enabled determining -the microliardness of metals -and
alloys at temperatures up to 1 300 OC in vacuum at loads of
2
5 - 100 g and tensile tests with stresses of 0 - 60 kg/mm
The authors studied with this equipment the influence of
temperature on the microhardness of nickel-phosphor and of
Card 1/5

Dependence of the ....
26576
Viz9/61/ooo/oWoog/015
C073/E335
chromium coatings using a load of 100 g. The coatinq were
produced on specimens of commercial iron IN 100 kg/mm The
nickel-phosphor coatings were deposted from a solution
consisting of 21 g/1. of nickel chloride, 24 g/l. sodium
hyperphosphite and 10 g/1. sodium acetate. The coatings
contained about 9% phosphor and were 40 - 50 11 thick. The
chromium coatings (35-40 ji thick) were deposted from a
standard electrolyte at 55 0C, using a current density of
2
35 A/dm The thickness of the coatings was more than 2.5
times the der)th of the indentation at the maximum test
temperature. The microhardness of the nickel--phosphor
coatings was tested at elevated temperatures directly after
the coatings were produced and after heating
to 4oo 0C and holding them at that temperature for 1 hour,
followed by cooling in air. Such a heat-treatment ensures
better adhesion between the coating and the surface of the
component and increases the hardness. The chromium coatings
were not heated. The hot microhardness of specimens from
Card 2/5
R'.

Dependence of the ....
26576
S/129/61/000/008/009/015
E073/E335
the steel X181- (KhVG) was tested after quenching and low-
temperature tempering (HRC 63-64). The obtained results enable
comparing the temperature dependence of the hardness of this
steel wlih that of the coatings. 15 indentations were made at
each test temperature with a sapphire inden~er (pyramid with
an angle of 1360). The results, H IL I kg/mM versus
temperature, OC, are plotted in Fig. I (Curve 1 - nickel-phosphor-,-
coatings without heat-treatment; Curge 2 - nickel-phosphor
coatings after heat-treatment at 40o C for 1 hour; Curve 3 -
chromium-plating; 4 - steel KhVC2, HRC 63). The results show
that nickel-phosphor coatings have the highest hardness in the
temperature range 150 - 350 OC and should be used for
improving the resistance-to-wear of components operating at
these temperatures. It is advisable to use chromium-plated
or hardened steels for components operating at temperatures
0
above 350
C-
Card 3/5

Dependence of the ....
26576
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E073/E335
There are 1 figure, 1 table and 6 references: 4 Soviet and
2 non-Soviet. The two English-language references quoted
are: Ref. 1 (in text) and Ref. 3 - M. Hansen, Constitution
of Binary Alloys, New York, 1958,
ASSOCIATIONS: Institut mashirnredeniye AN SSSR (Institute of
Machine Science of the AS USSR)
Vsesoyuznyy nauchno-issledovatellskiy institut
mekhanizatsii sel'skogo khozyaystva (All-Union
Scientific Research Institute for Mechanisation
of Agriculture)
Card 4/5

28899
3/129/61/000/010/001/012
E193/E48o
AUTHORS: Oding, I.A., Corresponding Plember AS USSR,
Lozinskiv.._b1.G,, Doctor of Technical Sciences,
Antipova, Ye.I., Engineer and Stepanov, V.N, Engineer
TITLE: A study of the mechanism of fracture of austenitic steel
in short-time service at 11000C
PERIODICAL: Metallovedeniye i termicheskaya obrabotka metallov.
no.10, 1961, 10-13 + 4 plates
TEXT-, Results are reported of short time (3 to 30 minutes),
constant-load and time-to-rupture tests, carried out at 11000C on
austenitic steels 3Xl8M9 (EKhl8Nq) W07% C, 180/0' Cr, 99.' Ni,
1.56% ma, 0,310? Si) and 4XlljHl4S2M (41'hl4Nl4V2M) (0,450'-' C,
111% Cr, 15,4 Ni'0 2,3u' IV, o,6o/,'. Mn and O,W..'. Si). The test; pieces
were preliminarily heat treated by heating for two hours at
1100*C in evacuated quartz ampules followed by oil quenching. (ne
face of each heat treated specimen was polished and etched to
reveal the microstructure and test pieces with an average grain-
size of 30 to 60 (EKhl8N9) or 100 to 130 microns (4KhlhNl4V2M)
were selected. During the tests (carried out in vacuum) the
etched side of the test piece, marked by a series of equi-Oi--tvirit,
Card 1/4

28899
S/129/61/000/010/001/012
A study of the inechanism E193/E480
(50 microns) microhardness indentations, was facing a window through
which microcinephotographs were taken throughout the duration of
each test. This made it possible to study each stage of the
deformation process by measuring the increase in the distance
between the diamond pyramid indentations, and by following the
changes in the microstructure. To overcome the difficulties caused
by volatilization of the test piece material and its subsequent
condensation as a metallic film on the window of the vacuum chamber,
a special device was constructed whose detailed description is given
in the paper. Some of the typical results are reproduced in
Fig.9, showing the strain (c, %) versus time (minutem) curves for
steel 4Khl4Nl4V2M tested at IIOOOC under a stress of 5.5 kg/mm2;
broken curve relates to the total elop~~ation of the test piece,
curves marked by numbers give the el-ingation of microregions
bounded by the corresponding diamonJ indenter marks as shown in the
insert in Fig.g. Other observations can be summarized as follows,
(1) The microstructure of the steels studied was revealed after one
minute at 11000C; this was most likely caused by preferential
volatilization of the metal in the grain boundary regions,
(2) Intergranular cracks appeared in the very early stages of
Card 2/4

A study of the mechanism
28899
S/129/61/000/010/001/012
E193/E480
deformation which indicated that, under the experimental conditions
employed, creep is associated mainly with int ercrysta I line slip with
very little deformation taking place within the grains.
(3) The total elongation depended upon the applied stress and
varied between 17.5and 25/o in steel EKhl8N9 and between 8 and 16%
in steel 41(hl4Nl4V2M. This difference was attributed to the
larger grain-size of the latter material.
(4) For an equal stress of 2.5 kg/mm2, the time-to-rupture was
5.5 and 24 minutes on steels EKhl8N9 and 4Khl4Nl4V2M respectively.
This difference was also attributed to the difference in the
grain-size, since the total length of the grain boundaries which
determine the strain accumulated prior to fracture is smaller in a
coarse-grained material. There are 9 figures and 3 Soviet-bloc
references.
ASSOCIATION: Institut metallurgii i Institut mashinovedeniya
AN SSSR (Institute of Metallurgy and Institute of
Science of Machines AS USSR)
Card 3/4

34534
S/659/61/007/000/021/044
D217/D303
AUTHORSg Sadovskiyp V-D-p Sokolkov? Ye.N.9
Petrova, S.N.9 Antipova, Ye.I,., Gaydukov, M.G.9 and
Mirmel'shteyn, V.A.
TITLE: Influence of thermo-mechanical treatment on the high
temperature strength properties of austenitic steel
SOURCE: Akademiya nauk SSSR. Institut metallurgii. Issledova-
niya po zharoprochnym splavam, v. 7, 19619 202-209
TEXT: A complex alloy steel of the austenitic class, widely used
in industry for manufacturing components for high temperature ser-
vice, was studied. During ageing of this steel, the complex chromi-
um and vanadium carbides responsible for its strengthening are pre-
cipitated. The material was heated to 1180 - 12000C and rolled at
1000 - 11000C at a speed of 5.7 m/min. After rolling, the billets
were immediately water quenched in order to prevent recrystallize-
tion. The cross-section of the billets obtained was 11.5 x 11,5 mm
their length, 70 mm, and the reduction due to rolling, 25 30
Card 1/4

S/659/61/007/"000/021/044
Influence of thermo-mechanical ... D217/D303
Control billets were heated simultaneously with those chosen for
thermo-mechanical treatmentg and were subsequently quenched from
the above temperaturc~ All billets9 whether thermo-mechanically
treated or only heated and quenched, were aged to a hardness of 310
- 320 HB. After heat treatmentg specimens for two series of -tests
were made from the billets. One series was used for studying struc-
ture during high temperature extension in vacuo. This also enabled
the degree of deformation to be determined and photographs of the
same portion to be taken at various stages of testing. Testing was
carried out in a IMASh-5M machine at 9000C and a stress of 9.5 '-g
/MM2, using specimens of 3 x 3 mm cross-section, heated -by direct
passage of current. The second series of tests, in which K.I, Tere-
khov participated, consisted of the standard tests for long-term
strength at 6500C and stresses of 35 and 38 kg/mm2, as well as at
7000C and a stress of 32 kg/MM2. For this purpose, specimens of
-,.rorking portion diameter of 5 mm and 50 mm length were used~ The
microstructure of each specimen was studied in conjunction with
these testeg particularly any peculiarities in structure appearing
after thermo-,mechanical treatment as compared with normal quenching-
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S/659/61/007/000/021/044
Influence of thermo-mechanical ... D217/D303
The distribution of deformation along the length of the specimen,
the intercrystalline and crystalline plasticity and the formation
and propagation of cracks during fracture were given particular
attention. It was found that high-temperature plastic deformation
of the steel investigated, under conditions in which recrystalliza-
tion processes are suppressed (thermo-mechanical treatment)q leads
to a considerable increase in long-term strength. The beneficial ac-
tion of thermo-mechanical treatment is associated with structural
characteristics of the steel which arise during high temperature
plastic deformation and are fixed by cooling at a sufficiently high
rate. Such characteristics are the complex geometry of grain boun-
dariesp grain fragmentation and further refinement of the fine cry-,
stal structureo These structural characteristics of the steel re-
tarded the development of fracture during creep, since (a) the cha-
racteristic serrated grain boundary structure retards the amalgama-
tion between micro.- and macro-cracks; (b) breaking-up of the fine
crystal structureq and an increase in the density of immobilized
dislocations render plastic deformation within the grains more dif-
ficult. There are 5 figures and 16 references: 15 Soviet-bloc and
Card 3/4
U7

S/659/61/007/000/021/044
Influence of thermo-mechanical ... D217/D303
1 non-.Soviet-.bloc. The reference to the English-language publica-
tion reads as follows: P.W. Davies and J.P. Dennison, J. Inst. Me-
talag 87, 49 1958.
V~/
Card 4/4

S/659/61/007/000/026/044
D217/D303
AUTHOR: Lozinskiy,.M.G.
TITLE; Present state and direction of future development of
high-temperature metallography
SOURCE: Akademiya nauk SSSR. Institut metallurgii. Issledova-
niya po zharoprochnym splavam, v. 7, 19619 233 - 241
TEXT: This paper deals with the present state of high-temperature
metallography techniques and with measures to be taken for the fur-
ther development of this phase of the science of metals. In the
first approximation, research carried out by means of high-tempera-
ture metallography can be classified as (1) techniques enabling the
microstructural changes of specimens to be studied during experi-
ments by direct observation through the microscope, and 2) methods
of studying the properties of materials without direct consideration
of microstructure. High-temperature metallography methods are divi-
ded into three groups: The first group comprises microstructural
investigations enabling the kinetics of grain growth to be observed
Card 1/2

S/659/61/007/000/026/044
Present state and direction of ... D217/D303
at selected heating rates or under isothermal soaking conditions,
and the study of development of polymorphic changes, the precipita-
tion of phases and the actual stages of development of corrosion
processes (by artificial addition of definite quantities of aggres-
sive media to a vacuum chamber in which the test specimen is placed
and by photographing the changes in color of individual grains and
grain portionsp arising due to color interference in this oxide
films)o The second group comprises methods for Etudying strength
properties at various rates of thermal and mechanical loading. The
third group embraces methods for determining many important proper-
ties of metals and alloys (hardness and microhardness, modulus of
elasticity and internal friction, thermal and electrical conducti-
vity, coefficient of expansion, intensity of evaporation, and dif-
fusion, etc.) in relation to temperature and time of testing. Me-
thods for the testing of hardness and microhardness at various tem-
peratures are particularly important. Modern instruments for measu-
ring hardness, microhardness, change in hardness on heating and de-
formation at high tmperatures and X-ray equipment are described.
There we 5 figures and 17 references: 16 Soviet-bloc and 1 non-So
viet-bloc.
Card 2/2

LOZINSKIY M.G. doktor tekhn.nauk;
S., inzh.
ZUSMANOVICH, (I.G., inzh.; MIROTVORSKIY,
Dependence of the microhardness of wear-resistant coatiogs on the
temperature. Metalloved. i term. obr. met. no-8:37-j9 Ag '61.
04IRA 14:8)
1. Institut mashinovedeniya AN SSSR i Vsesoyuznyy nauchno-
issledovatel'skiy institut mekh*anizatsii sellskogo khozyaystva.
(Protective coastings) (Metals, Effect of temperature on)

KISHKIN, S.T.; 1!~ZINSLI~_, M.G., doktor tekhn.nauk; BOKSHTEYN, S.Z., doktor
tekhn.nauk, prof.; ~dKOLKOV, YeAq kand.tekhn.nauk
Effect of Wh temperature plastic deformation on the mechanical
properties of nickel-base, heat-resistant alloys. Metalloved. i
term. obr. met. no.1:38-40 Ja '62. (MIRA 15:1)
1. Chlen-korrespondent AN SSSR (for Kishkin).
(Heat-resistant alloys--Heat treatment) (Deformations (Mechanics))
R

LOZINSKIY9 M.G. doktor tekhn.nauk; BERNSHTEYN, M.L., kand.tekhn.nauk;
MAYA, T.V., lnzh.
Investigating the polygonization of molybdenum by high temperature
metallography. Metalloved. i term. obr. met. no.1:57-64 ja '62.
(MIRA 15:1)
1. Institut mashinovedeniya Gosudarstvennogo komiteta Soveta
Ministrov SSSR po avtomatizatsii i mashinostroyeniyu i Moskovskiy
institut stali.
(Molybdenum--Metallography) (Dislocations in metals)

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metal 9
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TIMRMDM�CU"XCAL. TR&ATWvT OF STEM
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44,
4-11
'.to

37728
AUTHORS: Bokshteyn, S.Z.,
Sokolkov, Ye.N.
TITLE: Thermomechanical
manganese austenLtic
s/i8o/62/000/002/001/018
F-193/E383
Kishkin, S.T., Lozinskiy, M.G. and
(Moscow)
treatment of a chromium-nickel-
steel
PERIODICAL: Akademiya nauk SSSR. Izvestiya..' Otdeleniye
telchnicheskilch nauk. Metallurgiya i toplivo, no. 2,
1962, 15 - 21
TS,'-',T: The, so-called, "thermomechanical treatment" (TMO)
consists essentially of.combining plastic deformation at
J.e,-.i;-,)eratures above the recrystallization temperature with
quenching under conditions precluding recrystallization of the
plastically deformed material. The effect of this treatment on
the structure and properties of various materials has already
been studied by other workers. Some additional data on TI-10
of austenitic steels are presented in the present paper, with
particular reference to the properties of these steels after
TX'O to the ageingtreatment and to some characteristics of the
diffusion processes.- The experiments were:conducted on chromium-
Card 1/8 ,

Thermomechanical treatment, ....
S/180/62/000/002/001/018
E193/E383
nickel-manganese austenitic steel DLA 481 (E148i) specimens,
13 and 60 min in diameter, the former 150 and the latter 250 min
long. The plastic-deformation part of TMO was effected by
rolling at 2.4 in/min in the case of specimens 60 mm in diameter
and at 4-5,'7-5 and 13.5 m/min in the case of 13 mm diannoter
speciniens.. 25 and 30% reduction vras given in each case.
AL~crystalli:.Zation of the 13 min diameter specimens was suppressed
b,, im:nedi4te quenching in a water tank mounted on the rolls
i~he time interval bet-ween completion of the rolling
opei-ation'and quenching amounting to 0.2 to 0.3 sec. Rapid
cooling of the 60 nun diameter specimens was attained with the
aid of a 'especially designed spraying device. Preheating of
the test ~)ieces for rolling was done in air in an electric
furnace, the preheating temperature and time being 1 180 0C and
2 hours, irdspectively. TMO of small (13 min diameter) test
pieces I-r ' ' 18o to
q4',carried out after cooling them from 1
1 100 0C.,,-jIn the case of large (60 min diameter) test pieces
IfZ110 was 4j)plied at. the preheating temperature and after cooling
Card 2/ 3

s/18o/69/ooo/oWool/o18
Thermomechanical treatment E193/E383
to'l.150, 1 100, 1 050 and 1 000 0C. A number of test pieces
ivrere given conventional treatment (water-quenching) to obtain
control specimensifor comparison. Alil the test Pieceso(whether
quench-hardened of subjected to TMO) 'were aged at 68o C-for
10 liours, after 1'r ich they were-Siv-ei, an additional treatment
of 10 liours at 79~ OC, followed by aj;br-cooling so as to Attain
hardness corresponding to the indentAion diameter d
OTn
3.5 - 3.7 mm. In addition to standard tensile tests at room
tcmpera~ture, tests at 650 OC were carried out under conditions
of short and prolonged loading, the latter (i.e. creep) t2sts
being conducted under an applied stress of 39 or 43 kg/mm
To study and compare the progress of diffusion processes in
material subjected to~TMO or given the conventional treatment,
the rate of diffusion was measured by a radioactive-tracer
technique, entailing cutting a taper section across the diffusion
region. 59
A.-thin filn, of Fe was electrodepobited on the specimens studied,
which were then given a 150-hours diffusion-annealing treatment
0
at 800 C. In vacuum, afteir which both volume and grain-boundary
Card 3/8

js/i8o/62/ooo/oo2/ool/ol8
Thermomechanical treatment E193/F,383
diffusion coefficients were determined.- Overall diffusion
coefficients were also calculated with the aid of the
absorption method. Phase-analysis was usedto study the effect
of hot plastic deformation on the process of carbide-formation
during ageing,. Electrolytic extraction of the carbide phase
from various -test pieces was carried out in a 501o' solution of
hydrochloric -iac:Ld in methanol. The anode residues urerWalso
e.-camined by X-ray diffraction measurements. Prelimiriafy
e.:amination of the microstructure revealed that, irrespec-'L'.ive
of the rolling sp .ed employed duringTNIIO, full suppression of
recrystallizationThad been-achieved #1 small (13 mm diampter)
test pieces only.4 None of the TMO procedures used on-laf-ge
(60 mra diameter) test pieces had ensured suppression of the
recrystall:ization process. The results of standard tensile tests
at 20 and 650 OC, carried out on small specimens, sho-ved that
T`.-M brou-'at about a slight increase in UTS at 20 0 (from
103 - 114 kg/mm2) but had z1o effect on the strength of steel
at 650 0C. The variation in plasticity was somewhat different.
Card 4/8

S/180/62/000/002/001/018
Thor-mortiechanical treatment E193/E383
.Thus, as the rolling speed during TIMO increased, the elongation
of steel at room temperature decreased below that of specimens
:-ieat--treated in the conventional manner and then increased to
c.-:ceod this value. The same applied to reduction in area vrhich,
a"or TIMO entailing deformation by rolling at 13.5 m/min, attainod
a val-ac of 33.20,'), i.e. 250,C' higher than the value attained after
conventional treati-.ient. The results of tensile tests at 650 oc
also showed a slight increase in elongation of specimens
subjected to TMO, although reduction in area of specimens
rolled at 13.5 m/min -t-,ras somewhat lower than that of the control
.est pieces. The results of,accelerated creep bests conducted
on small test pieces under a stress of 43 kg/mri showed that
irrespective of the conditions during TMO, the time-to-rupture
of the steels studied increased after this treatment by 20-255%.
The corresponding increase for specimens tested under a stress
2
OA. 59 amounted to 60o%. Metallographic examination of
small specimens shoi-ted that recrystallization during T~10 had
been completely suppressed in each of the specimens examined.
TIiis vras indicated by the absence of new small crystals which
Card 5/8

S/180/62/000/002/001/018
Thermomechanical treatment .... E193/E383
,.-.,ere usually formed in recrystallized material along t,-Ie
boundaries'-of the original grains. A common specific structural
.eature of all specimens subjected-to TMO was distoition of
grain boundaries -whlch had assumed a characteristic serrated
contour. A distinguishinS feature of specimens rolled during
T"-~O at a speed of 4-5 m/min vas -well-developed sub-structure.
T*-c formation of sub-structure was associated with the for;-.iation
o-
blocIzz (several tens of microns In size) In the interior of
4---e -rains. The relatively large angula:r misalignment of these
-1 ~~
bloc'~s was indicated by the ease vrit'a which the block boundaries
Could be revealed by etching. No such clearly defined sub-
structure was observed in specimens rolled during TA'10 at higher
speeds, although in a few isolated instances there was some
evi(~ence of block formation. The formation of the 'Aine structure
could be attributed to poly.-onization processes and subsequent
decorat-L'on of the low-angle boundaries by the solute atoms and
second-phase particles Another specific feature of the stkruc-~-,Ire
-produce(I by TIM 0 is thel fragmentation of grains, i.e. sub-division
Card 6/8

s/18o/62/000/002/001/018
T:lCrI1,10mcchanical treatment E193/E383
L~r.-.ins into parts whose dimension are commeasurable with
_11C size of t1le grains. thems elves. It would appear that
_zaZmentatioa is mainly a result of intensive tviinnine.~,taking
-)lace durin- hot plastic deformation.. As stated already, none
of t`ic T%,O procedures applied to large (60 rmi, diameter) test
.)iaccs ensured complete suppression of recrystallization, the
extent of i-;hich increased with depth -So that an unrecrystallized
structure was observed only in the very surface layers of the
;*.iaterial. In-this case TMO had practically 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 increased considerably, it was
independent of the rolling speed employed in-the-course of this
treati--ient. The vanadium-carbide content of the material was
practically unaffected by TMO. Finally, the results of diffusion
studies indicated that after TMO the coefficient of volume
c:iffusion of iron in steel'at 800 0 C increased fourfold. Since,
to a general increase in the diffusion mobility, difficulties
--;-ore
i encountered in determining the grain-boundary diffusion
Card 7/8

s/i8o/62/ooo/oo2/ooi/oi8
Thermoi-,iechanical treatment .... E195/E383
coefficient, the overall diffusion coefficients were measurdd
by the absorption method. Comparison of the results obtained
.L.or test pieces with different structures showed that the
overall diffusion coeffi cient for materials which had undergone IV11
T.T-10 u-as more than t-vice as high as that for specimens given the
conventional treatment. The general conclusion reached was
-_r' in addition to the previously established strengthening
ef oct of -rain-boundary distortion caused by Tl-,'LO,, tao benefici.11
er-oct of this treatment on the high-tomperature properties of
z t c c I wa sassociated urith an increase in the quantity of the
strengthening phase and, possibly, with refinement of the mosaic
I
structure aud formation of slight*texture. There are 4 figures
and 2 tables.
'SUBMITTED: October 11, 1961
Card
Z~~Q'

-33464
S/129/62/000/001/007/011
LIU E073/E335
AUTHORS: Kishkin, S.T., Corresponding Member of the AS.USSR,
Lozinskiy. M.G., Doctor of Technical Sciences,
ff_o_kihteyn_,_,-.Z., Doctor of Technical Sciehces,Professoz~
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 Metallovedeniye i termicheskaya obrabotka metallov,
no.l,.1962, 38-40 + I plate
TEXY: Two Ni-Cr-base alloys were investigated: the low-carbon
3OH437ra (E1437B) alloy of the standard composition and the
D"617 (E16I7) alloY, containing 0.12% C and additions of W and
Mo. The alloy EI437B was subjected to the following thermo-
mechanical treatment: blanks of 16 mm diameter were first soaked
for 8 hours-at 10800C and rolled at this temperature at a 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 austenite-
Card. 1/4

33464
Influence of ...
S/129/62/000/001/007/011
E073/E335
and to retain the structure, produced as a result of high-
temperature plastic-deformation. The blanks were then
aged at 7000C for 16 hours. Blanks of the alloy E1617 were
heated to 1200% and stamped in a press
so that an avera
e
,
g
reduction of 30% was achieved; this was followed by-quenching
in water. The blanks were then aged-at 8000C for 16 hours.
The results of static tensile and impact tests-at room
temperature are given in Table 1. Studies of the influence of
thermomechanical treatment on the creep strength of austenitic
steels revealed that recrystallization should be prevented
during high-temperature plastic deformation since it would
cancel out the beneficial effects of the thermomechanical
treatment. Midrostructural investigations correlated
with the results of mechanical tests indicate that the increase- in
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/E335
structure of the material and to texturing. -The large increase
in the ductility of-the investigated alioys is obviously due
to the ab sen6e of intercrystalline fracture. The following
participated in the experiments: N.I. Korneyev; T.A.Gordeyeva,
Ye.I. Razuvayev, O.N. Podvoyskaya, M.N. Kozlova,
L.M. Strlzhevskaya, T.A. Volodina, N.F. Lashko, E.V. Polyal~,
G.N. Korableva, A.V. Bulanov, M.I. Spektor and I.G. Skugarev.
There are 2 tables and 7 references: 4 Soviet-bloc references
and 3 non-Soviet-bloc. The three English-language references
mentioned are: Ref. 4: E.B. Kula, J.M. Ohosi - "TASM", v152,
1960; Ref. 5: D.J.Schmatz, J.C. Shyne, V.F. Zackay - Metal
Progress, v-76, no. 3, 1959; Ref. 7: E.B. Kula, S.L. Lopata
Trans. AIME, V-215i 1959-
Card 3A

Influence of ....
Table 1:
33464
S/129/62/000/001/007/011
E073/E335
Mechanical Properties
Alloy 'Treatment 0D.2, 4r- 6 9 ak9 HB
2 bl2 41 2 (d-
kg/ps kg/mm % % kgm/cm OEM
mm)
EI437B Standard (reference
specimens) 97.0 25o0 20,9 -
TMO 1* 119 32oO 300',7 - -
Standard (reference
E1617 specimens) 71.7 103.7 14.6 io.1 1.8 3.6
TMO 93.8 129.6 31.'2 25.9 7.8 3.35
Plastic.deformation of supercooled austenite
followed by conventional hardening and tempering
Card 4/4 treatment.

33468
S/129/62/000/001/011/011
19-124, 14 51,1 1 !; 7-1 14 1 E193/E383
AUTHORS: Lozinskiy. MiG., Doctor of Technical Sciences,
ff-ernshteyn, M.L., Candidate of Technical Sciences
and Vershinskaya, TiV., Engineer
TITLE: Polygonization of molybdonum studied by high-
temperature metallographic methods
PERIODICAL: Metallovedeniye i termicheskaya 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 improve-
ment in the mechanical properties, both at room and elevated
temperatures. This is particularly important in the case of
Mo, which is mainly used in high-temperature applications and,
consequently, it is important to establish heat- and mechanical-
treatment procedures which would ensure polygonizgtion of this
metal and its alloys. Hence the present investigation, in
which high-temperature metallograph:Lc methods such as described,
Card l/

Polygonization of ....
33468
S/129/62/000/001/011/011
E193/E383
for instance, in Ref. 6 (M.G. Lozinskiy and N.Z. Pertsovskiy -
Izv. AN SSSR, OTN, seriya Metallurgiya i toplivo, no. 1, 1961)
were used. Experiments were conducted on -racuum-melted Mo
containing small additions of Ti and Zr which constituted a
solid solution and in which no solid transformation of any kind
took place. Thecast ingots were first hot-forged and then
hot-rolled to 3.5 mm thickness, after which the material was
annealed at 1 500 OC for one hour. Part of the annealed strip
was rolled at 600 0C to 5 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 0in
vacuum at a constant rate of strain at 1 050 and 1 150 C 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 elevated
temperatures. The results obtained can be summarized as
Card 2/

33468
S/129/62/000/001/oll/oll
Polygonization of .... E193/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 lower
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
plast�c deformatlon (%) be�ng ind�cated on each graph;
experimental points denoted by circles, triangles and dots
relatea 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 deformed to 139 reduction is
higher at 1 150 0C than at 1 050 0C 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 3/
'W'

33468
S/129/62/000/001/011/011
Polygonization of .... E193/E383
of the alloy. In Fig- 3 the decrease in hardness (8 H, kg/mm 2
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 m1crohardness (HV, kg/mm.2) is glotted against the
loidims time at 1 050 (graph a) and 1 150 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 maximum at 30 and 80 min,
respectively. The maximum 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 analysis show that
fragmentation of blocks in the course of plastic deformation is
a characteristic feature of Mo and that the degree of
Card 4/
Ps. 3
t
i7i
N,