SCIENTIFIC ABSTRACT YUSHKEVICH, P. M. - YUSHKIN, N. P.

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• Collection: Scientific Abstracts
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• Document Creation Date: November 2, 2016
• Document Release Date: September 19, 2001
• Sequence Number: 8
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

//j 0 6761
0
14P. 07/ 00 ,
soy/126- 8-6-17/24
AUTHOR: Yushkevich, P.M.
TITLE: - The T~qture of the Hardening of Hardened RiL_11! Speed
Stee,:LXDuring Tempering
PERIODICAL: Fizika metallov i metallovedenlye, 195.9, vo,l 8, Nr 6,
pp 8!)6-903 (USSR)
-,'PSTRACT-. There are two schools of thought on the cavise of
secondary hardening: one (Ref .1 to 4):.attributes this
effect to secondary martensite,transfo'rmati,on, the
secohd (Ref 5,6) includes other factox~s. The.object of
the present work was to elucidate the :hatuve of secondary
hardness and red hardness of high-speed steel, tile more-
exact determination of .carbide-transfo'r'mation temperature-
ranges and the study of changes in thd fine crystal
Thr e steels,
structure of the alpha- and gamma-phasesi
I
'
~
d
84

ere use
w
n d J
.1
,
j
flexperime
typei5 R 18,~~150 R 18\ tal) an
-
-

17-
50, 0.87% C;
'Wp-ective compositions being: 0-:7
the re : 3T
4.2, 4.3. 7-5% Cr.; 18.9i 18.01 4.9% W; 1.2, 1.6, 1.2% V;
0.28,.0.26, 0.32%.Mn; o. 16, o. 15, 0 - 17%, S i
O.Oll, O.Olo, o.ol6% s; 0.030, 06027,: 0.02.5% P-
Specimens were hardened in oil and iced-water from
0

Card 1/4 fo
C r
austenizatlon- temperatures at 1290, 1200 and 1240

67669
soir/126-8-6-17/24
The Nature.of the Hardening-of Hardened High-Spead. Steel During
Tempering
R 18, 150.R~18 and El 184, respectively. Measurement of
crystal lattice parameters. blocks and II and III form of
'distortion was effected on 1. mm diameter round and
x 8 x 20 mm flat specimens, in a powder. camera
(149 mm diameter holder) and a type UPS-501 ionization
installation- with iron radiation. Fil Ishows for
R-18 steel as functions of temperature the hardness
(curve 1). percentage of carbon in martensite (curve 2)
(Ref 7), block size (curve 3)1 overall, distortion (curvc
and II type distortions (curve 5). The rate of block-
growth for the same steel is shown in,:Fig 2 as a function
of tempering temperature. Fig 3 givepa more detailed
picture of the variation of the propel-ties studied in
relation to number and duration of.teraperings at 560*C
after hardening-from 1290 (continuous~lines) and from
1260'*C (interrupted -lines). In Fig 41similar information
is given for -150 -R IS steel for the g4.imma (continuous
lines)-and alpha (interrupted linesYlphase.s. The
investigation of martensite decomposition iin EI 184 ste-al
Card 2/4 showed the fine structure to be similixr to' that of

67669
SOV/126-8-6-17/24
Tito MA turo -of U105 Hard on fit gof Ste,41 Dux4ng
Tempering
R 18 steel but the rate of block growlih is greater in
the,former.-Finally, the author discusses. the red
hardness of the steel, The authorconcludes that
secondary hardness results notfrom tiransformation of
residual austenite Into secondary'martensite but mainly
from dispersion hardening of primary and secondary
martenaite., The softening which.occu.rs ir. the first
pericid of tempering is accompanied by a diffusion-less
expartsion of the residual austenite lattice followed by
a contraction due.to loss mainly of carbort but also of
alloying elements. When the steel on-tempering attains
maxivium hardness the II type distorti ons :In the alpha and
gammet phases become equal to 4-0 - 4-5 x 10-3. The
activation energy calculated from the alplia-phase block-
growth rate is 6o kcal/mol and 80 kce',i/mo:L for 540 to 620
and'above 650*Cs respectively. Two forms of concentration
heterogeneity.have been found: in tempering martensite
at 380 to 520% and in ferrite at 560 to 15400C. ,
Card 3/4 Therf) are 4 figures, Itable and 14 So .viet references# LK

67669
SOV/126-8-6-17/24
The Natu,re of the Hardening of Hardened High-Speed Steel During
Temporing
ASSOCIATION:Ukraiiaskiy,nauchno-issledovatellskiy.trubliyy institut
(Ukrainian Scientific-Research Institute for Tubes)
SUBMITTED: May 4, 1959
-Card 4/4

s/i85/6o/oo5/oo1/o1 1/0 18
()4]r 14 Ak A151/AO29
MTHORUl- YU
On the, Seoendary Hardness and Red gardness of High-Speed Steel
PFRIODICAL8 Ukrayiaslkyy Fizychnyy Zhurnal, 1960, Vol- 5, No- 1, PP- 100 163
TE rx The alin of this paper is toclarify the naturt4 of the secondary
harlnr-ss and red hardness of hIgh-apeed steel, to specify thetemperature inte;.-
vale of carbide conversiorLa and to study the conversions in a thin crystalline
atruoture. of. ot- 9d y-phases. The following three grades of high-apeed steel
were selected for investigations P18 (Ri8), 150P18 (15OH18) arid.911-184 (EI-184).
'The chemical composition of these steels is given in a table. The samples were
hardened in oil with throwing them into cold water at temperatures of austenite
treatment equalling 1,2900C for R18,, 1,2000C for 15OR18 and 1,2400C for EI-184.
The tempering was conducted In a vacuum furnace.. 144-d-tice parameters, coherent
dispersion zones (of blocks) and the distortions of the II and III type were
measiared. on round samples with a diameter of I mm and a flatnei3s of 4 x 8 x 20
IJM.IAll-this was doae ~n a powder cell with an adapter measurIng 14.0 m EAbstm-
:or 3-notes the diameter of 149 m is probably a mistake and should be 149 mml,
"axd 1/3

S/185/60/005/0131/-311/0'18
A151AD29
On tbe Secondary Hardness apd Red Hardnass of High-Speed Steel
and. in an iron emission by using YPC-50H (URS-501) ionization installation.
measun&ments of the nizes of blocks and.of the distortions of the II type were
made according to the lines (110) anl...(211) of the ot-phase and (111) and (311)
of the y-phase on the basis of -the met-hod. given in Referenf~es 10 and 11 under
-the conaitian that the intensity distribution is described by Gauss' funotloi;_'
Lattice parameters and the quantity of the remaining austanite were checked ac-
'cordtng to the lines (110) and (Ill), as well as the.lin6a (211) and (311). 11,
was ascertained that the secondary hardness.1s.not the result tof the conversicri
of the remaining austenite into a?aecondary,one, but the, ult of a dispersica
hardening, bo -thof the initial and secondary martensits.- The disperslon harden-
ing of the remainin. g austenite is of minor importance ' The increase in the
hardness of steel taking place in the Istarting period of tempering is accompanied
by a diffusion-free widening of the remainitt austenite lattice. Further, this
widening is replaced,by a compression of the% lattice which ocemrs owing to a
deconcentrat ion of the rem-aining austenite-chiefly by carbon and partly by al!W.-
ing elements. When t~e maximum hardness is achieved in steel during the temper-
ing process, the distortions of the 11 type in the oL- and y-phtses coincide. and
become 4 4.5 lo-3 cm. The parameters of a fine crystal st:ructure have been
Card-Z/3

3/185/60/005/001/011/018
A151/11029
~iie Secondary Hariness and Red Hardness of High-Speed Steel
q'!i-4F-.rmin,?dp Vnich chBracterize a high hardness and red hardnei3s of the tempered
6-teel. T,,ie activation energy was calculated according to the data of
1-.- I:,.,.,;re.-%se rate cf cC-phase blocks within the temperature range of 540 - 620OC;~
j., ~e 14cal/mole. At more than 6500C, the activatioft enerv is 80-kcal/ipole.
Tv- types of concentration non-homogenelty were revealed,in nuixtensite within
36ij - 54-OOC and in ferrite within 560 - 6400G~ In the case oT tempering at%'C;~.?
the heigtit of thr -:arricentration non-homogeneity in f6rrite depends on the height
of the temperatur_a of tempering. There Arel. 1 table, 4 figuires and 14 Soviet
references.
A S&X, T A T. TON niu~ov4-1-daalldnyy trubnyy inoty-tut (Ukraln,,-An ScIter,
llrlv Vilwie' I'.
~"ard 3/3

18"1500 775c)].
SOV~! PC) -f)'0-2 -4/1~
(Eng, ncer)
AUTHOR: ZLJ~
TITLE: Alteration of Fine Crystal Structure of' Residual
Austenite at Tempering,of High-Speed Steel
PERIODICAL: Me allovedeniye i termicheskaya obrabotny mettalov,
10W, Nr 2, pp 14-20~!(USSR)
ABSTRACT: Tempering of high-speed steels changes the structure
of residual austenite and, consequently, the trans-
formation of the lat ter to marten-olte becomes retarded.
The ;author studied the structure change- that took
place when forged steels,R18 and 150R18 and hot rolled
steel EI184 (see Table below) were tempered at various
temperatures. The first and third steels were aLlSterii-
t,Ized In barium chloride salt bath ~it 1P80 to 12900C
and the sedond.steel in vacuum at 1190 to 1200 0 C.
Then all three were quenched in oil, and a 0.5 mm
thick surface layer etched off. The unit'cell
Card 116

Al'teration of Fine :~Vrystal Structure of 775191
Residual Austenilte at Tempering of High-Speed SOV/129-6o-2-4/13
Steel
dimensions, size of blocks, structure distortions,
and their changes were computed according to X-ray
diffraction data obtained with camera URS-501., and
measured with talc rophotometer DIT-4. The identity
period of unit cells of residual austerilte in steel
1118 proved to Lncveat3e by maxImum 0,016 A (Fig. 1)
regardless of the temperature of tempei~ing, but the
maximum was achieved in shorter time at higher
td&A C he j CC-,OC'J"r'8Aj 07P
Bra. J)
0A . C Mn 90
S t' I-Crj W_ I_., S,
R18. 0:73 4 18 '9 1:2 0:28 0,16 0:011 0430 18-22
1 0 027 70-73
150RIEI.; 1 5 4:'3 18 1 6 0 26 0.15 001
a 18.1 0,87 7,5 4,0 1,2 0,32 0,17 0,016 0.025 55-60
Card 2/6

Alteratio-t) of Fine! Crystal Structure of 7759 1.
Re,sidual Auatenite at Tempering of High-Speed SOV/129-6o-2~.-4/i3
Steel
tempering temperatures. The-increase of unit cell
dimensions was not caused by diffusion. The maximum
Increase of austenite unit cells in steel B1184
tqa~i 0.006 A, Steel 150R18,ti.-Mpored at;,,5400C.-or.-hIgher,'.
-deer se--.of- --the'Aden t i ty--pe riod- of-- aus ten I te- by- -
ea
rd A'
.-012 -7-The~ --of -.z he 'un dimen-'*
mait um.. 0. _j~ cell
-,ncrea e
ontE~-Of th-the 'first- two.steeis--,
seems to be accompanied by the decomposition of mart ensite
whose diffraction lines become narrower, and by relocation
of structure distortions as the result of.which the
-volume-per unit-mass of martensite demreases.- Having
reached the maximum, the identity period of austenite
-begins.to decrease apparently because of partial loss
of its carbon content and of contaminated metals,'by
diffusion. The unit cells of austenite stabilize after,~
certain period of temperingif its temperature is below
0
5000 C; if above 500 C, continuous l0as of carbon leads
Card 3/6

Alteration of Fine Crystal Structure of 77591
Residual Austenite at Tempering of High-Speed. SOV/129-6o-2-4/13
Steel
1 1 3.625
T7
3.615 OF
I'd
3,
3,615
J, FIS -
J, I to Jul,
TTIL 0,4
I'm 540*1
5 10, JO I 1 5 U JO I 1 3915
Soo
0.2
0 1 4 6 8 f0 12 14, hri
Fig. 11. Change oflattice
constant ol' residual
austenite In steel R18
during tempering.
Card 4/6 -Fig. It. Relationship between
carbon content and lattice
constant of'residual austenite
in steel 15OR18, and the duration
of repeated'tempering 540, 5060,
580, and 6200 C.

Alteration of Fine Crystal Structure of 77591
Residual Austenite at Tempering of High-Speed SOV/129-60-2-4/13
Steel
to the formation of secondary martensite. In steel
159R18, the decrease of unit cell,dimensions of
residual austenite, austenite decomposition by 18
to 212%, It,,, partition into a larger nurabor of blooko,
the structure distortions, and the subsequent gain fn
streng.th, advance during early stages of tempering at 5600
C; but after a time austenite blocks begin to grow at
the expense of carbides and the strength reduces.
Tempering at various temperatures proved the dependence
of the austenite to martensite transformation in
steel 150R18 on,a certain point of structure distortions
(0-31 A in this steel) above which the transformation
-point drops, and below,.rises. Thus,~the transformatio -n
point characterizes the degree of structuredistortions.
The latter hinder the coherent rearrangement of the
structure from - to -phase, and stabilize residual
austenite; the carbon content of auatehite stabilizes
after a certain drop (Fig. 4.). Tempering of steel
BI184 below, 5000 C causes austenite partition Into
Card 5/6

Alteration of Fine Crystal'Structure of 77591
Residual Austenite at Tempering of High-Speed -SOV/!L29-60-2-4/13
Steel
blocks until a certain stable stage jis reached, the
partition hardly te kes place above 5000 C. Hydrostatic
compression of.residual austenite displaces Fe
atoms f-rom their equilibrium positions by maximum
A. However, since compr4osion *tresses at
tempering act for only 5 to 20 second.s, they hardly
affect austenite to martensite transformation. There
are 6 figures; 1 table; and 16 references, 12 Soviet,
2 German, 1 U.S., 1 U.K. The U.S. and U.K. references
,are: Cohen, M., Koh, K., "TASM", Vol 27, Nr 4 (1939);
Goldschmidt., H ) "Journal of the Iron~and Steel Instu.",
Vol 186 (1957):
ASSOCIATION: Ukrainian Scientific Research Pipe Institute
(Ukrains,ecty nauchno-ts3ledovatells.kiy,trobnyy ln3titut)
Card 6/6

8/021/60,/000/008/008/011
MW305
AIUTHORt Yushkavychp P.M*
TITID On chan%s in the substructure of haxdened high'-sp .eed
steel*when tempering
PERIODIOAL:-Akademi a nauk Ukrayinalkoyi-MR, Dopovidit noa,8#
19600 N64 1661
EXT: The aim of the paper isto study the fine.-crystal strue Iture
~of high speed steel,.-In his ex eriments the author used OPI-184 (BI
-184)t P-18 (R-18) and 150P18 T150R18) steels aei .shown in the Ta-
ble. As the:result of.detailed studies of hardneest concentration
of heterogeneity Aet/a, blocks of a-phase, distortions of second
type and amount of carbon in a-solutionsp the tempering of the
martensite could be oub-divided in four stages.*1) For temperatu-
res-200-20000# the mechanism is similar to carbide steel. 2) At
iremperatures 2000-54000P the further precipitation of carbon from
'the martensite took plece; starting with temperature 3800 cementi-
Oard 1/4

&�31W
81021,1601000100810081011
On changes in the substructure D210/D3,05
too were enriched in ohromium.1 chromium carbidais.together with the
concentration of heterogeneity of martensite we:ve formed# 3) At
temperaturet3-5400-620'009-carbide-*of-cementits type converted into
oarbide-of va#adivii and wolfram# followed consequently by a con-
centration of heterogeneity in ferrite. From 624)0-65000 carbides
were intensively enriched in va*adium and wolfriun. Ties between a-
'hak-d solution and carbide lessens and blocks of~a-phase split.
From 6,500-7600 the-blooke increase conaiderablyll-diatortione of Il
tybe relax and transormation y no, a + k takes place. The decrease
of,residual austenite took place at.all stagest except the first.
'Tho lattice parameter of residual austenite inexeases in the first
stage-from 3607 - 303-1 bee- so%V the increaite in II and 11 type
au
distortions its growth slowly decreases in the other stages. At
50000 the lattice parameter stabilize-at this coxad be explained by
.the-equilibrium between an -oversaturated hard solution and carbi-
ded of the cementite type. The author.compared the distortions of
III-type, during multiple tempering at 54009 5600p 5800C with the
temperature of martensite transformationst and obtaining the foi-
Card 2/4

S/02Y60/000/008/008/011
On changes in the substructure V210 D305
lowin~g results:,l) It point decreases (5400),then -FU 0. 37 1;
2) If N doesInot changet then Vii 0-31 A; ~ 3) if MH increases
then 1/71-2 = 0.25 1. The position of the martensite point depends on
the distortion of the III type which arises during the secondary
martensite transformations. Therefore# distortions of II-type in
the residual audtenite rectrain considerably the traLsformations
austenite ---o martencito. By this pioperty the tempering of resi-
dual austenite differs from overcooled austenite, in which distor-,
tions.of the III type are absent. There are 5 figures, 1 table and
9 references: 7 Soviet-bloc and 2 non-Soviet-blace The references
to the English language publications read as follows: X. Kye,
Journal of Iron and Steel Institute 174, 49 ~659-1953; GOD.-Gold-
schmidt, Journal of the Iron and Steel Institute, 1869 1t 1957.
ASSOCIATION: Ukr. n-d trubnyy instytut (Ukr n-d.Pipe Institute)
PRESENTED: by K.F. Starodubovp Academician UkrSSR
SUBTAITTED:- July-13t 1959
Card 3/4

3/137/62/000/003/141/191
A0521AI01
AUTHOR: Yushkevinh P
TITIX; _Gn the methods of determining II kind distortions and block sizes
PERIODIML. RefvrativnZrr --huriiial, Metallurgiya, no, 3, 1962, 69, abstract 31447
(V sb, "Proiz-vo trub". Kharlkov, Metallurgizdat, no, 4, iq6i,
134 -142)
TEXT: Tho existing motbods of dfAormining, 11 kind ditutortions AXI&