U.S. patent number RE28,645 [Application Number 05/412,625] was granted by the patent office on 1975-12-09 for method of heat-treating low temperature tough steel.
This patent grant is currently assigned to Nippon Steel Corporation. Invention is credited to Koichi Aoki, Tohru Inoue, Hiroshi Mimura, Hiroshi Sakurai, Seinosuke Yano.
United States Patent |
RE28,645 |
Aoki , et al. |
December 9, 1975 |
Method of heat-treating low temperature tough steel
Abstract
.[.Heat.]. .Iadd.In the disclosed heat.Iaddend.-treating method
of hot-rolled steel plate containing .Iadd.less than 0.20% of C,
0.05 to 0.40% of Si, 0.10 to 5.0% of Mn and 1.50 to 10.0% of Ni
.Iaddend..[. 1.5% to 10.0% Ni and 0.1% to 5.0% Mn and further at
least one element selected from the group consisting of Mo, Cu, Cr,
Nb and V, at need and.]. .Iadd.with .Iaddend.the balance being
substantially Fe, .[.comprising subjecting one or more time
repeatedly said.]. .Iadd.the .Iaddend.hot-rolled steel plate .[.to
heating.]. .Iadd.is heated to .Iaddend..[.and sequent quenching
from.]. a temperature .[.within.]. .Iadd.between .Iaddend.the
.[.range between.]. Ac.sub.1 and Ac.sub.3 .Iadd.transformation
.Iaddend.points .Iadd.and then cooled, whereafter .Iaddend..[.,
then subjecting.]. the steel plate .Iadd.is subjected .Iaddend.to
tempering treatment at a temperature below .Iadd.the
.Iaddend.Ac.sub.1 point .Iadd.but sufficiently high so as to cause
precipitation or formation of fine austenite, .Iaddend.thereby to
improve .[.largely.]. toughness at low temperature and .Iadd.to
.Iaddend.obtain excellent workability.
Inventors: |
Aoki; Koichi (Yokohama,
JA), Yano; Seinosuke (Kamakura, JA),
Mimura; Hiroshi (Tokyo, JA), Inoue; Tohru (Tokyo,
JA), Sakurai; Hiroshi (Kawasaki, JA) |
Assignee: |
Nippon Steel Corporation
(Tokyo, JA)
|
Family
ID: |
27021838 |
Appl.
No.: |
05/412,625 |
Filed: |
November 5, 1973 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
Issue Date |
|
Reissue of: |
776421 |
Nov 18, 1968 |
03619302 |
Nov 9, 1971 |
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|
Current U.S.
Class: |
148/621; 148/653;
148/663; 148/662 |
Current CPC
Class: |
C21D
6/001 (20130101); C22C 38/08 (20130101) |
Current International
Class: |
C22C
38/08 (20060101); C21D 6/00 (20060101); C21d
001/26 (); C21d 007/14 () |
Field of
Search: |
;148/12F,12.4,134,143
;75/123 |
References Cited
[Referenced By]
U.S. Patent Documents
Primary Examiner: Stallard; W.
Attorney, Agent or Firm: Toren, McGeady and Stanger
Claims
What is claimed is:
1. A heat-treating method for producing a steel having an excellent
toughness at an extremely low temperature and .[.a.]. high strength
and good workability.Iadd., .Iaddend.from a steel consisting
essentially of less than 0.20 wt.% C.[...]..Iadd., .Iaddend.0.05 to
0.40 wt.% Si, 0.10 to 5.0 wt.% Mn, 1.50 to 10.0 wt.% Ni as basic
.Iadd.alloying .Iaddend.component.Iadd., with the balance being Fe
and the usual impurities, .Iaddend.comprising subjecting a
hot-rolled steel plate having the said composition to a
heat-treatment comprising heating to a temperature between the
Ac.sub.1 transformation point and the Ac.sub.3 transformation point
and a subsequent cooling from the said temperature at least at an
air cooling rate and thereupon tempering the steel plate at a
temperature below the Ac.sub.1 transformation point.[...].
.Iadd.but sufficiently high so as to cause precipitation or
formation of fine austenite. .Iaddend.
2. A method according to claim 1, wherein the heat-treatment
comprising the heating of the hot-rolled steel plate to a
temperature between the Ac.sub.1 transformation point and the
Ac.sub.3 transformation point and the subsequent cooling from the
said temperature is carried out .[.repeatedly.]. more than one
time.
3. A method according to claim 2, wherein prior to said
heat-treatment, said hot-rolled steel plate is subjected to a solid
solution treatment.
4. A heat-treating method for producing a steel having an excellent
toughness at an extremely low temperature and .[.a.]. high strength
and good workability from a steel consisting essentially of less
than 0.20 wt.% C, 0.05 to 0.40 wt.% Si, 0.10 to 5.0 wt.% Mn,
.[.to.]. 1.50 to 10.0 wt.% Ni as basic .Iadd.alloying
.Iaddend.components .Iadd.with the balance being Fe and the usual
impurities.Iaddend., comprising heating a hot-rolled steel plate
having the said composition to a temperature below the austenite
grain coarsing temperature .Iadd.but .Iaddend.above the Ac.sub.3
transformation point and subsequently cooling the steel plate from
the said temperature at least at an air-cooling rate, then
subjecting the steel plate to a heat-treatment comprising heating
the steel plate to a temperature between the Ac.sub.1
transformation point and the Ac.sub.3 transformation point and
subsequently cooling said steel plate from the said temperature at
least at an air cooling rate and thereupon tempering the steel
plate at a temperature below.[.. .Iadd.the Ac.sub.1 transformation
point but sufficiently high so as to cause precipitation or
formation of fine austenite. .Iaddend.
5. A heat-treating method according to claim 4, wherein the
heat-treatment comprising the heating of the steel plate to a
temperature between the Ac.sub.1 transformation point and the
Ac.sub.3 transformation point and the subsequent cooling from the
said temperature at least at an air cooling rate is carried out
.[.repeatedly.]. more than one time.
6. A heat-treating method according to claim 4, wherein said
hot-rolled steel plate is subjected to a solid solution treatment
prior to heating the steel plate to a temperature below the
austenite grain coarsing temperature .Iadd.but .Iaddend.above the
Ac.sub.3 transformation point and subsequently cooling the steel
plate from the said temperature.
7. A method as claimed in claim 1 wherein said steel further
comprises at least one element selected from the group consisting
of 0.05 to 1.0 wt.% Mo, 0.1 to 2.0 wt.% Cu, 0.1 to 1.50 wt.% Cr,
less than 1.0 wt.% Nb, less than 1.0 wt.% V and less than 0.05 wt.%
sol. .[.Ao.]. .Iadd.Al.Iaddend., and the rest being Fe and
unavoidable impurities.
8. A method as claimed in claim 4, wherein said steel further
comprises at least one element selected from the group consisting
of 0.05 to 1.0 wt.% Mo, 0.1 to 2.0 wt.% Cu, 0.1 to 1.50 wt.% Cr,
less than 1.0 wt.% Nb, less than 1.0 wt.% V and less than 0.05 wt.%
sol. Al and the rest being Fe and unavoidable impurities.
Description
BACKGROUND OF THE INVENTION
1. Field of the Invention
The present invention relates to a heat-treating method for
imparting .Iadd.to a low carbon tough steel containing 1.5 to 10.0%
by weight of Ni and 0.1 to 5.0% by weight Mn .Iaddend.a very high
toughness at low temperature, particularly at such an extremely low
temperature as -196.degree.C, the boiling point of liquid nitrogen,
and an excellent workability, particularly low yield ratio at room
temperature .[.to a low carbon tough steel containing 1.5 to 10.0
wt.% Ni and 0.1 to 5.0 wt.% Mn.]..
2. Description of the Prior Art
It is well known that recently a 9%-Ni steel .Iadd.has been
developed which .Iaddend.is widely used as a steel material for use
at low temperature. This 9%-Ni steel is usually .[.made.].
.Iadd.manufactured into .Iaddend.a finished product after
.Iadd.having been .Iaddend.subjected to hardening and tempering
treatments.Iadd., .Iaddend.or to normalizing and tempering
treatments.Iadd., .Iaddend.after a solid solution treatment. The
thus treated product shows a relatively good toughness at low
temperature, but .[.it does not always follow that a.].
satisfactory result.Iadd.s .Iaddend.can .Iadd.not always
.Iaddend.be obtained in case an optimum toughness.Iadd.,
.Iaddend.superior to the above-mentioned.Iadd., .Iaddend.is
required.
As regards .[.to.]. workability, no particularly excellent result
could be obtained according to the experiments made by the
inventors of the present invention.
Further.Iadd., .Iaddend.a 6%-Ni series low temperature tough steel
has been developed by the inventors of the present invention as a
low temperature tough steel which should take the place of the
9%-Ni steel.[., and.]..Iadd.. .Iaddend.For this new steel U.S. Pat.
No. 3,388,988 was granted. By subsequent investigations, however,
it was discovered that in order to obtain an optimum
toughness.Iadd., .Iaddend.a tempering treatment must be carried out
under the optimum conditions of a relatively narrow range, which
.[.make a knotty point in the operation.]. .Iadd.is cumbersome from
an operational point of view.Iaddend.. Also as regards the
workability, the optimal result could .Iadd.still .Iaddend.not
.[.still.]. be secured with the 6%-Ni steel.Iadd., .Iaddend.as
.[.in.]. .Iadd.is .Iaddend.the case .[.of.]. .Iadd.with
.Iaddend.the 9%-Ni steel.
.[.Now, as seen from examples of 6%-Ni and 9-Ni steels, in general,
with.]. .Iadd.When .Iaddend.a usual heat treatment .[.which is to
be.]. .Iadd.is .Iaddend.carried out .Iadd.with 6%-Ni and 9%-Ni
steels .Iaddend.for obtaining a high toughness.Iadd., .Iaddend.the
yield ratio becomes high, but a steel having a high yield ratio is
.[.used to be detested by a.]. .Iadd.not favored by
.Iaddend.construction designer.Iadd.s .Iaddend.from the view point
of safety. As is explained in the following, the present invention
.[.is to.]. provide.Iadd.s .Iaddend.a heat-treating method, by
which a steel having a high toughness can be obtained in .[.the.].
.Iadd.a .Iaddend.wide .[.range of a.]. tempering temperature
.Iadd.range.Iaddend., while keeping the yield ratio low by
utilizing a segregation.
SUMMARY OF THE INVENTION
The present invention .[.is to.]. eliminate.Iadd.s .Iaddend.the
above-mentioned defects of Ni-containing steels. Therefore, the
primary object of the present invention is to provide an excellent
tough steel which .[.is by far.]. .Iadd.has significantly
.Iaddend.improved .[.in the.]. toughness .Iadd.characteristics,
.Iaddend.by causing .[.an.]. .Iadd.a .Iaddend.Ni-containing steel
to form a fine structure according to a method .[.mentioned.].
.Iadd.explained .Iaddend.in the following, without causing thereby
a reduction in .[.a.]. strength at low temperature.
The second object of the present invention is to impart an
excellent workability, particularly a .[.property of.]. low yield
ratio.Iadd., .Iaddend.to .[.an.]. .Iadd.a .Iaddend.Ni-containing
tough steel.
Another object of the present invention is to provide a tempering
treatment .[.of an.]. .Iadd.for a .Iaddend.Ni-containing steel with
the optimum conditions .[.of.]. .Iadd.in .Iaddend.a wide.[.r.].
range.
Still other objects of the present invention will become manifest
by the following description.[.s.]. with reference to the examples
and accompanying drawings.
The present invention.Iadd., .Iaddend.which is to attain the
above-mentioned objects.Iadd., .Iaddend.provides the method,
wherein a hot-rolled steel plate containing 1.5 to 10.0% Ni, 0.1 to
5.0% Mn, and Si in an amount as required for making steel
(preferably 0.05 to 0.4%) and further .Iadd.containing .Iaddend.at
least one element .[.properly.]. selected from the group consisting
of 0.05 to 1.0% Mo (a part or the whole of Mo may be replaced by
W), 0.10 to 2.0% Cu, 0.10 to 1.50% Cr, less than 0.05% sol, Al,
less than 0.2% Nb, less than 0.2% V, less than 0.1% Zr, less than
0.1% Ti, less than 0.005% B, as .Iadd.the .Iaddend.occasion
demand.Iadd.s.Iaddend., and the balance being Fe and unavoidable
impurities.Iadd., .Iaddend.is heated to a temperature above the
Ac.sub.3 transformation point .[.and.]. .Iadd.is .Iaddend.then
cooled with a cooling rate greater than .Iadd.obtained by air
.Iaddend..[.a.]. .Iadd.obtained by air .Iaddend.cooling .[.by
air.]. and thereafter is heated to a temperature between the
Ac.sub.1 transformation point and the Ac.sub.3 transformation point
and .Iadd.is .Iaddend.then cooled (with a cooling rate greater than
.[.a.]. .Iadd.obtained by air .Iaddend.cooling .[.by air.].) .[.and
then.]. .Iadd.whereupon .Iaddend.the thus treated steel plate is
further subjected to a tempering treatment at a temperature below
the Ac.sub.1 transformation point.[.,.]. .Iadd.; .Iaddend.or the
hot-rolled steel material may be directly heated to and quenched
from a temperature between the Ac.sub.1 transformation point and
the Ac.sub.3 transformation point, .[.and then.]. .Iadd.whereupon
.Iaddend.the thus treated steel plate is subjected to a tempering
treatment at .Iadd.a .Iaddend.temperature below the Ac.sub.1
transformation point. Further, prior to the heating and cooling to
and from a temperature above the Ac.sub.3 transformation point or
to and from a temperature between the Ac.sub.1 transformation point
and the Ac.sub.3 transformation point.Iadd., .Iaddend.a solid
solution treatment may be carried out.
BRIEF DESCRIPTION OF THE DRAWINGS
FIG. 1 is a diagram showing the relation between .[.a.]. tempering
temperature and .[.a.]. toughness of a 6%-Ni series steel treated
according to the method of the present invention.Iadd., .Iaddend.as
compared with that of a 6%-Ni series steel treated according to a
conventional method, i.e., quenched and tempered.
FIG. 2 is a photograph showing a structure by the observation with
an electron microscope of a magnification of 4,500 of a 6%-Ni
series hot-rolled steel plate as heated to 800.degree.C. (above the
Ac.sub.3 transformation point) and cooled therefrom.
FIG. 3 is a photograph showing a structure by the observation with
an electron microscope of a magnification of 4,500 of .[.in the
case where.]. the steel of FIG. 2 .[.is.]. .Iadd.after having been
.Iaddend.further heated and sequently cooled to and from
670.degree.C.
FIG. 4 is a photograph showing a structure by the observation with
an electron microscope of a magnification of 4,500 of .[.in the
case where.]. the steel plate of FIG. 3 .[.is.]. .Iadd.which has
been .Iaddend.further subjected to a tempering treatment at
600.degree.C.
FIG. 5 is a photograph showing a structure by the observation with
an electron microscope of a magnification of 4,500 of .[.in the
case where.]. the steel plate of FIG. 2 .Iadd.which .Iaddend.is
directly subjected to a tempering treatment at 600.degree.C.
FIG. 6 is a diagram showing the relation between .[.a.]. tempering
and .[.a.]. toughness of a 9%-Ni series steel treated according to
the method of the present invention.Iadd., .Iaddend.as compared
with that of a 9%-Ni series steel treated according to a
conventional method.
FIG. 7 is a photograph showing a structure by the observation with
an electron microscope of a magnification of 4,500 of a 9%-Ni
series hot-rolled steel plate as heated to 800.degree.C. and cooled
therefrom.
FIG. 8 is a photograph showing a structure by the observation with
an electron microscope of a magnification of 4,500 of .[.in the
case where.]. the steel plate of FIG. 7 .[.is.]. .Iadd.after having
been .Iaddend.further heated to 670.degree.C. and sequently cooled
therefrom.
FIG. 9 is a photograph showing a structure by the observation with
an electron microscope of a magnification of 4,500 .Iadd.of
.Iaddend..[.in the case where.]. the steel plate of FIG. 8 .[.is.].
.Iadd.which is .Iaddend.subjected to a tempering treatment at
575.degree.C.
FIG. 10 is a photograph showing a structure by the observation with
.[.must be.]. .Iadd.an .Iaddend.electron microscope of a
magnification of 4,500 .[.in the case where.]. .Iadd.of
.Iaddend.the steel plate of FIG. 7 .Iadd.which has been directly
heated .Iaddend..[.to directly 6.]. to 575.degree.C. and sequently
cooled therefrom.
FIG. 11 is a photograph showing a structure by the observation with
an electron microscope of a magnification of 4,500 .[.in the case
where.]. .Iadd.of .Iaddend.a 3%-Ni series hot-rolled plate
.Iadd.which .Iaddend.is subjected to the heat-treatment method of
the present invention.
FIG. 12 is a photograph showing a structure by the observation with
an electron microscope of a magnification of 4,500 .[.in the case
where.]. .Iadd.of .Iaddend.a 3%-Ni series hot-rolled steel plate
.Iadd.which .Iaddend.is subjected to hardening and tempering
treatments.
DESCRIPTION OF THE PREFERRED EMBODIMENT
The essential feature of the present invention resides in producing
a structure consisting of a fine ferrite and tempered martensite,
wherein a stable ultrafine austenite or cementite is
precipitated.Iadd., .Iaddend.by subjecting a hot-rolled steel plate
containing necessary elements in the ranges as above mentioned or a
steel plate obtained by hardening or air-cooling the hot-rolled
steel plate.Iadd., .Iaddend.to special heating and cooling
treatments to and from a temperature between the Ac.sub.1
transformation point and the Ac.sub.3 transformation point and
thereupon subjecting the thus treated steel plate to a tempering
treatment, which enables the steel to display an excellent
toughness at a very low temperature.
.[.It was manifested by the.]. .Iadd.The .Iaddend.investigations
made by the inventors of the present invention .Iadd.demonstrated
.Iaddend.that a relatively good toughness could be displayed even
at low temperature, when a tough steel containing Ni in a
relatively great amount, as a 9%-Ni steel or a 6%-Ni steel, was
subjected to hardening and tempering treatments. However, it was
further discovered that, if a hot-rolled steel plate having the
composition as above mentioned was subjected to a heat treatment
specified by the present invention, that is heating to a
temperature within a range between the Ac.sub.1 transformation
point and the Ac.sub.3 transformation point and sequent quenching
or air-cooling from the said temperature, .[.there could be
obtained such an.]. excellent toughness at low temperature and
workability .[.as was never seen at any.]. .Iadd.values were
obtained which were far superior to those displayed by the
.Iaddend.conventional Ni-containing steel.Iadd.s, such .Iaddend.as
9%-Ni steel or 6%-Ni steel.[.,.]. .Iadd.. .Iaddend..[.whereby the
application of.]. .Iadd.The inventive .Iaddend.steel .[.for use.].
.Iadd.is therefore particularly suitable for use .Iaddend.at low
temperature .[.was widely spread.].. Further, as such a remarkable
improvement in the toughness at low temperature as above mentioned
could be obtained without adding new alloy element.Iadd.s.Iaddend.,
that is, with a steel having the composition in the same or even
.[.smaller.]. .Iadd.narrower .Iaddend.ranges as the conventional
9%-Ni steel or 6%-Ni steel, a very economical production of an
excellent tough steel for use at low temperature was made
possible.
In the process of manufacturing the steel of the present
invention.Iadd., .Iaddend..[.a.]. melting may be carried out in any
well known steel-making furance such as converter, open-hearth
furnace, electric furnace, high frequency furnace and the like.
There is no problem .[.in the point.]. .Iadd.in respect .Iaddend.of
melting. A molten steel prepared by melting in any of the said
furnaces is regulated in its composition by adding alloy elements
as required and is made to a hot-rolled steel plate through the
steps of ingotting, slabbing and hot-rolling. Then, the thus
obtained hot-rolled steel plate is heat-treated as specified by the
present invention.
The starting material .[.of.]. .Iadd.for performing .Iaddend.the
present invention is a hot-rolled steel plate as above mentioned.
In the present invention, the hot-rolled steel plate may be
immediately subjected to the special heat-treatment of the present
invention (a solid solution treatment may be carried out prior to
this special heat-treatment) or, .[.as another method.]. .Iadd.in
another embodiment.Iaddend., the hot-rolled steel plate may be
heated at first to a temperature above the Ac.sub.3 transformation
point but below the crystal grain coarsening temperature, with or
without the solid solution treatment to be carried out prior to
this heat-treatment. In this case, it is not desirable to heat the
steel plate to a temperature above the crystal grain coarsening
temperature, because the toughness of the steel will be
deteriorated thereby. This heating is followed by .[.a.]. cooling
rate greater than .[.an.]. .Iadd.obtained by .Iaddend.air-cooling,
that is, quenching, or by .[.an.]. air-cooling. The structure of
the steel after this treatment .[.becomes.]. .Iadd.is that of
.Iaddend.a martensite structure or a mixed structure of martensite
and bainite (or a mixed structure of martensite, bainite and
ferrite according to circumstances).
The steel plate as hot-rolled or further subjected to the
heat-treatment to a temperature above the Ac.sub.3 transformation
point and sequent quenching or air-cooling as above
mentioned.Iadd., .Iaddend.is further successively heated to a
temperature in the range between the Ac.sub.1 transformation point
and the Ac.sub.3 transformation point and sequently quenched or
air-cooled.
The essential feature of the present invention is just this special
heat-treatment, that is, a heating to a temperature between the
Ac.sub.1 transformation point and the Ac.sub.3 transformation point
and sequent cooling from the said temperature. By this
heat-treatment a fine structure of the steel is produced, whereby
the toughness as well as the workability of the steel can largely
be improved without reducing the strength thereof at low
temperature. That is, when the above-mentioned steel plate as
hot-rolled or further subjected to the heat-treatment to a
temperature above the Ac.sub.3 transformation point and sequent
quenching or air-cooling, is further successively heated to a
temperature in the range between the Ac.sub.1 transformation point
and the Ac.sub.3 transformation point, a fine austenite, enriched
in C, Ni, Mn and N.Iadd., .Iaddend.present as an impurity, is
precipitated .Iadd.or formed .Iaddend.in an insular form at an old
martensite crystal grain boundary, old austenite crystal grain
boundary or ferrite subgrain boundary.Iadd.. .Iaddend..[.with the
help of an effect of accelerating the.]. .Iadd.The precipitation or
formation of the fine austenite is facilitated by the effect of
accelerated .Iaddend.diffusion caused by the presence of a great
number of dislocation groups in the quenched or air-cooled
structure which is a result.[.ed from.]. .Iadd.of .Iaddend.the
previous treatment.[.,.]..Iadd.. .Iaddend..[.and this.]. .Iadd.This
.Iaddend. austenite is equilibrated with well annealed and fine
ferrite having an excellent toughness, resulting in the formation
of a mixed structure of .[.them.]. .Iadd.fine austenite and fine
ferrite.Iaddend.. In the present invention it is an indispensable
condition that the mixed structure of austenite and ferrite is
produced by the heating to a temperature between the Ac.sub.1
transformation point and the Ac.sub.3 transformation point. The
most preferable range in the above-mentioned heating to a
temperature between the Ac.sub.1 transformation point is
620.degree. to 800.degree.C. .[.in the case of.]. .Iadd.if
.Iaddend.the steel .[.having.]. .Iadd.has .Iaddend.the composition
range as above mentioned. Through the sequent quenching or
air-cooling.Iadd., .Iaddend.a mixed structure of ferrite and fine
insular martensite can be obtained. The quenching or air-cooling
from the above-mentioned temperature range may be carried out once
or may be repeated several times. By repeating the said treatment
several times the martensite structure is further refined, whereby
the toughness of the refined steel is all the more improved. The
medium for use in the quenching may be water, oil, mist or any
other .Iadd.medium .Iaddend.which .[.can perform.]. .Iadd.causes a
compulsory cooling. There is no particular limitation in the medium
to be selected.
The thus heat-treated steel plate is then tempered at a temperature
below the Ac.sub.1 transformation point, preferably in the range of
450.degree. to 600.degree.C. By this tempering treatment.Iadd.,
.Iaddend.austenite is again dispersedly precipitated .Iadd.or
formed .Iaddend.in a very fine form in the fine martensite islands,
and there is finally produced a mixed structure of a pure ferrite
.Iadd.which is the result .Iaddend.of .[.resulted from.]. the
advanced tempering, a tempered martensite and an extremely fine
temper-formed .Iadd.or reverted .Iaddend.austenite, whereby the
toughness of .Iadd.the .Iaddend.steel at lower temperature is
largely improved, without causing .[.the.]. reduction of the
strength.
However, in the case of the steel containing Ni in a small amount,
for instance, less than 4.0 percent and less than 3.5 percent Mn,
and the sum of Ni and Mn being less than 4.5 percent, there is
found no appearance of the temper-formed .Iadd.or reverted
.Iaddend.austenite, but .Iadd.instead .Iaddend.the precipitation of
fine cementite in the above-mentioned islands of tempered
martensite. The ferrite matrix is also purified, on account of the
tempering being well advanced, and becomes a structure .[.rich in
the.]. .Iadd.which also exhibits great .Iaddend.toughness.
.[.too.]..
In the following there will be briefly explained the reason .[.of
having limited.]. .Iadd.for limiting .Iaddend.the amounts of
.Iadd.the .Iaddend.alloy elements to be contained in the steel of
the present invention.
C is effective .[.on.]. .Iadd.for .Iaddend.improving the
hardenability and further elevating the stability of austenite at
low temperature, as .Iadd.it is .Iaddend.being absorbed into the
austenite precipitated during the tempering treatment. However, if
the C content is too .[.much.]. .Iadd.high.Iaddend., .Iadd.the
.Iaddend.amount of solid solution carbon in the ferrite matrix will
increase, which impairs not only the toughness, but also the
weldability of steel. Therefore, the C content .[.was.]. .Iadd.is
.Iaddend.limited to less than 0.2 percent.
Si is an element necessary for steelmaking and is usually contained
in an amount of more than 0.05 percent. However, if .Iadd.it
.Iaddend.exceeds 0.4 percent, there .[.appears the.]. .Iadd.is a
.Iaddend.tendency .[.of the.]. .Iadd.that the .Iaddend.toughness
.[.being deteriorated.]. .Iadd.of the steel may
deteriorate.Iaddend..
It is well known that Ni is a useful element for improving the
toughness and strength of steel. Further, it serves to stabilize
the temper-formed .Iadd.or reverted .Iaddend.austenite at low
temperature, as .Iadd.it is .Iaddend.being absorbed into austenite
during the tempering treatment. However, if .Iadd.too much
.Iaddend.Ni is added .[.too much.]., .[.it.]. .Iadd.the steel
.Iaddend.becomes expensive. Therefore, the upper limit thereof
.[.was.]..Iadd.is .Iaddend.limited to 10.0 percent. On the other
hand, if .[.it.]. .Iadd.the Ni content .Iaddend.is less than 1.5
percent, the structure which is the object to be attained by the
present invention can not be obtained. Therefore, it is necessary
to .Iadd.provide a steel which .Iaddend.contain.Iadd.s .Iaddend.Ni
is an amount of at least more than 1.5 percent .[.,.]..Iadd.;
.Iaddend..[.and.]. and the preferable range is 4.5 to 9
percent.
Mn .[.serves to.]. not only improve.Iadd.s .Iaddend.the
hardenability, but also.Iadd., .Iaddend.like Ni and N,
stabilize.Iadd.s .Iaddend..[.a.]. .Iadd.the .Iaddend.very fine
austenite precipitated .Iadd.or formed .Iaddend.during the
tempering treatment and .[.elevated.]. .Iadd.increases .Iaddend.the
toughness and strength of the ferrite matrix. However, if .[.it.].
.Iadd.too much Mn .Iaddend.is contained .[.too much.]. .Iadd.in the
steel.Iaddend., it stabilizes carbide up to a considerably high
temperature. Consequently, the upper limit .[.thereof was.].
.Iadd.for Mn is .Iaddend.limited to 5.0 percent. Further, Mn is
useful as an element which can replace Ni. Therefore, the range
.[.of adding.]. .Iadd.for the .Iaddend.Mn .Iadd.addition
.Iaddend.is to be properly decided .[.depending.]. .Iadd.in
dependence .Iaddend.on the Ni content. For instance, if Ni is
contained in a range of 4.0 to 7.5 percent, it is .[.preferably.].
.Iadd.preferable .Iaddend.to .[.contain.]. .Iadd.add .Iaddend.Mn in
an amount of more than 0.9 percent. But.[.,.]. in case Cu is added,
the lower limit of Mn can be extended to 0.5 percent. On the other
hand, in case the Ni content is less than 4.0 percent, there is a
possibility of austenite being precipitated .Iadd.or
formed.Iaddend., if Mn is added in .Iadd.a .Iaddend.relatively
large amount, that is, more than 1.0 percent. But.[.,.]. in
.[.this.]. .Iadd.the latter .Iaddend.case, that is, in the case of
the Ni content being less than 4.0 percent, there is almost
precipitated cementite, if the sum of Ni and Mn is less than 4.5
percent. Therefore, in adding Mn, the above-mentioned conditions
must be taken into consideration in order to obtain the desired
structure. Further, in case Ni is contained in a large amount, Mn
may be added in a small amount. .[.At least with 0.1% Mn, the.].
.Iadd.The .Iaddend.object of the present invention can be achieved
.Iadd.with at least 0.1% Mn. .Iaddend.Therefore, the lower limit of
Mn .[.was decided to.]. .Iadd.is set at .Iaddend.0.1 percent.
Mo has .Iadd.the .Iaddend.effect.[.s.]. of extending the optimum
tempering temperature to the higher side, .Iadd.of
.Iaddend.refining the distributed states of temper-formed .Iadd.or
reverted .Iaddend.austenite grains and .Iadd.of .Iaddend.promoting
the diffusion of Mn, C and N. The addition of Mo is also effective
to prevent temper embrittlement. For this purpose Mo must be added
in a range of 0.05 to 1.0 percent. The same effect can also be
achieved, .[.even.]. when a part or the whole of Mo is replaced by
W.
Cu may be added, as the occasion demands, in order to improve the
corrosion resisting property and the toughness of the steel. Like
Ni and Mn, also Cu is thought to be effective .[.on.]. .Iadd.for
.Iaddend.stabilizing the temper-formed austenite and .Iadd.for
.Iaddend.strengthening some .Iadd.of the .Iaddend.solid solution
ferrite matrix .[.itself.]. proper. For this purpose .[.it.].
.Iadd.Cu .Iaddend.may be added in an amount of less than 2
percent.
Cr is added, as .Iadd.the .Iaddend.occasion demands, in order to
improve the strength of .Iadd.the .Iaddend.steel. Further, it is
useful for extending the optimum tempering temperature to the
higher side. It is necessary to be added in an amount of 0.1 to 1.5
percent.
Al is necessary to fix nitrogen contained in .Iadd.the
.Iaddend.steel as an impurity, besides being added as a deoxidizer.
Al may be replaced by at least one of other nitride-forming
elements such as Be, Nb, V and Ta and the like. If the Al content
is, however, too .[.much.]. .Iadd.high.Iaddend., the impact
property .Iadd.of the steel .Iaddend.at low temperature .[.of
steel.]. is .[.deteriorated.]. .Iadd.impaired.Iaddend.. Therefore,
.Iadd.the .Iaddend.Al .[.was.]. .Iadd.content is .Iaddend.limited
to 0.05 percent in the form of acid-soluble .[.one.].
.Iadd.Al.Iaddend..
Further, in the present invention at least one element selected
from the group consisting of less than 0.20% V, less than 0.2% Nb,
less than 0.1% Zr, less than 0.1% Ti and less than 0.005% B
.Iadd.may be present .Iaddend.for the purpose of .[.particularly.].
imparting .[.the.]. strength to .Iadd.the .Iaddend.steel and
.Iadd.for .Iaddend.promoting the effect of refining crystal
grains.
In the following the examples of the present invention shall be
.[.shown.]. .Iadd.described.Iaddend..
Table 1
__________________________________________________________________________
HEAT TREATMENTS AND MECHANICAL PROPERTIES OF 6% Ni SERIES STEELS
Chemical composition (wt. percent) Plate thick- Steel Sol. Other
ness, No. C Si Mn Ni Mo Al element mm
__________________________________________________________________________
6A 0.07 0.23 1.70 6.0 0.20 .[.0.15.]..Iadd.0.015.Iaddend. Balance
Fe. 12 6B 0.07 0.23 1.70 6.0 0.20 .[.0.15.]..Iadd.0.015.Iaddend. do
12 6C 0.07 0.23 1.70 6.0 0.20 .[.0.15.]..Iadd.0.015.Iaddend. do 12
6D 0.07 0.23 1.70 6.0 0.20 .[.0.15.]..Iadd.0.015.Iaddend. do 12 6E
0.07 0.23 1.70 6.0 0.20 .[.0.15.]..Iadd.0.015.Iaddend. do 12 6F
0.07 0.23 1.70 6.0 0.20 .[.0.15.]..Iadd.0.015.Iaddend. do 12 6G
0.07 0.23 1.70 6.0 0.20 .[.0.15.]..Iadd.0.015.Iaddend. do 12
6H.sup.1 0.07 0.23 1.70 6.0 0.20 .[.0.015.]..Iadd.0.015.Iaddend. do
12 6I 0.09 0.23 1.10 5.94 0.21 0.01 do 13 6J 0.09 0.23 1.10 5.94
0.21 0.01 do 13 6K 0.09 0.23 1.10 5.94 0.21 0.01 do 13
6L.Iadd..sup.1.Iaddend. 0.09 0.23 1.10 5.94 0.21 0.01 do 13
6M.sup.1 0.09 0.23 1.10 5.94 0.21 0.01 do 13 6N.sup.1 0.09 0.23
1.10 5.94 0.21 0.01 do 13 6O 0.064 0.11 0.52 6.30 0.22 0.01 Cu
0.84; 13 balance Fe. 6P.sup.1 0.064 0.11 0.52 6.30 0.22 0.01 do 13
6Q 0.10 0.23 1.70 6.0 0.20 0.01 Nb 0.05; 13 balance Fe. 6R .sup.1
0.10 0.23 1.70 6.0 0.20 0.01 do 13 Steel Heat treatment No. Q L T
__________________________________________________________________________
6A 700.degree.C. .times. 60 mm. WQ 550.degree.C. .times. 60 mm WQ
6B do 600.degree.C. .times. 60 mm WQ 6 C 800.degree.C. .times. 60
mm. AC. 670.degree.C. .times. 60 mm. WQ 500.degree.C. .times. 60 mm
WQ 6D do. do 550.degree.C. .times. 60 mm WQ 6 E do. do
600.degree.C. .times. 60 mm WQ 6 F do. do 625.degree.C. .times. 60
mm WQ 6 G do. do 650.degree.C. .times. 60 mm WQ 6 H.sup.1 .Iaddend.
.[.do.]. .Iadd. 600.degree.C. .times. 60 mm WQ 6 I do.
.Iadd.670.degree.C. .times. 60 mm. WQ.Iaddend. 500.degree.C.
.times. 60 mm WQ 6 J do. do 600.degree.C. .times. 60 mm WQ 6 K do.
do 625.degree.C. .times. 60 mm WQ 6 L.Iadd..sup.1.Iaddend.
.Iaddend. .[.do.]. .Iadd. 500.degree.C. .times. 60 mm WQ 6 M.sup.1
.Iaddend. .[.do.]. .Iadd. 600.degree.C. .times. 60 mm WQ 6 N.sup.1
.Iaddend. .[.do.]. .Iadd. 625.degree.C. .times. 60 mm WQ 6 O
800.degree.C. .times. 60 mm. WQ .Iadd.670.degree.C. .times. 60 mm.
WQ.Iaddend. 600.degree.C. .times. 60 mm WQ 6 P.sup.1 .Iaddend.
.[.do.]. .Iadd. do. 6 Q 800.degree.C. .times. 60 mm. AC.
640.degree.C. .times. 20 .[.mm.]. .Iadd.hr..Iaddend. do. 6
R.Iadd..sup.1.Iaddend. do. 625.degree.C. .times. 60 mm WQ
Mechanical property
__________________________________________________________________________
Elongation Y.R. Total Uniform Steel .sigma.y, kg./ .sigma.B, kg./
(.sigma.y/.sigma.B) elongation elongation No. mm.sup.2 mm.sup.2
percent percent percent vE-196.degree.C Hv kg.m/cm.sup.2
__________________________________________________________________________
6 A 25.5 6 B 26.2 6 C 77.9 89.9 0.87 24.2 12.5 5.75 6 D 71.7 83.6
0.86 28.4 15.1 31.3 6 E 69.9 81.4 0.86 29.8 15.3 29.8 6 F 56.4 87.4
0.64 31.9 20.1 26.0 6 G 57.0 98.5 0.58 26.0 15.3 9.0 6 H.sup.1 69.6
77.8 0.96 24.9 10.8 13.0 6 I 70.7 82.9 0.85 24.2 13.8 24.4 6 J 65.6
76.7 0.86 27.4 16.4 27.1 6 K .[.55.2.]..Iadd.56.2.Iaddend. 80.2
0.70 29.9 22.3 23.8 6 L.Iadd..sup.1.Iaddend. 79.5 84.2 0.94 20.5
7.6 6.5 6 M.sup.1 69.4 76.5 0.91 26.4 14.6 18.8 6 N.sup.1 63.3 75.1
0.84 26.0 15.6 26.1 6 O 22.5 236 6 P.sup.1 10.0 250 6 Q 17.5 297 6
R .sup.1 12.3 278
__________________________________________________________________________
.sup.1 Steels treated according to conventional methods Remarks:
Heat treatment: Q means a treatment of heating and cooling to an
from a temperature above the Ac.sub.3 transformation point; L means
a treatment of heating and cooling to and from a temperature
.[.below the Ac.sub.1 transformation point.]. .Iadd.between the
Ac.sub.1 transformatio point and the Ac.sub.3 transformation
point.Iaddend.; T means a tempering treatment at a temperature
below the Ac.sub.1 transformation point; .degree.C. is temperature,
mm is heating time (minute), WQ is quenching b water, and AC is
cooling by air. Mechanical property: .sigma.Y is Yield stress;
.sigma.B is Tensile strength; Y.R. (.sigma.Y/.sigma.B) is Yield
ratio; vE-196.degree.C. is V-notch Charpy impact test
value-196.degree.C. Hv is Vickers hardness. .Iadd.hr is heating
time (hour).
EXAMPLE 1
In table 1 there are shown mechanical properties of about 6%
Ni-containing steels, subjected to the heat treatment of the
present invention. All .Iadd.the .Iaddend.samples consist.[.ing.].
of steel plates having a prescribed thickness .[.respectively.].,
as .[.are.]. shown in table 1, .Iadd.and .Iaddend.have been
prepared according to .Iadd.a .Iaddend.conventional melting
process, ingotting, slabbing and hot-rolling.
Among them, the samples Nos. 6A and 6B are steels which contain 6%
Ni and 1.7% Mn. .[.and are.]. .Iadd.These samples were
.Iaddend.obtained by directly subjecting a hot-rolled steel to the
L-treatment (the treatment of heating and cooling to and from a
temperature between the Ac.sub.1 transformation point and the
Ac.sub.3 transformation point). The L-treatment is followed by the
T-treatment (tempering at a temperature below the Ac.sub.1
transformation point). In the case of the sample No. 6A the
tempering temperature was 550.degree.C. and in the case of the
sample No. 6B 600.degree.C. Both samples show an excellent
toughness at low temperature. .[.respectively.]..
The sample Nos. 6C to 6G are those obtained by subjecting a hot
rolled steel plate to the Q-treatment at 800.degree.C. for 1 hour
(the treatment of heating to and cooling from a temperature above
the Ac.sub.3 transformation point) followed by the L-treatment at
670.degree.C. and thereafter by the T-treatment at 500.degree. to
650.degree.C. respectively. The sample No. .Iadd.6.Iaddend.H is a
reference steel, which was not subjected to the L-treatment.
Concerning mechanical properties of each sample of No. 6C to 6G
treated according to the method of the present invention, there are
shown excellent values for the toughness at low temperature in
spite of a variety of tempering temperature. The reference steel
No. 6H shows only a value less than .[.a.]. .Iadd.one .Iaddend.half
of that of the sample No. 6E of the present invention, even though
the sample No. 6H was subjected to the T-treatment under the same
conditions as the sample No. 6E. From this comparison the above
mentioned .Iadd.advantages .Iaddend.will be easily understood.
Further, by the application of the method of the present invention,
the range of tempering temperature can be largely widened. In FIG.
1 there are shown the relations between the impact value and
tempering temperature on steels of the above-mentioned samples Nos.
6C to 6G (shown by a mark) as compared with steels treated
according to conventional methods, in which the L-treatment was
omitted (shown by a mark). As is evidently seen from this figure,
according to the treating method of the present invention.Iadd.,
.Iaddend.a tempering treatment for obtaining high impact values can
be carried out extending over a far wider range, as above
mentioned, whereby .[.a.]. .Iadd.the .Iaddend.difficulty in the
producing process .Iadd.to the effect .Iaddend.that the tempering
treatment must be carried under much narrower conditions, as was
heretofore .Iadd.the case.Iaddend., can be eliminated. Moreover,
the samples Nos. 6C to 6G show a very low yield ratio respectively,
which is particularly manifest in contrast to the sample 6H. It can
.[.be.]., therefore, .Iadd.be .Iaddend.concluded from the foregoing
that steels treated by the method of the present invention are
superior in the workability .[.to.]. .Iadd.as compared to that of
.Iaddend.conventional steels.
The samples Nos. 6I to 6N show the results .[.of.]. .Iadd.with
heat-treated .Iaddend.steels having the Mn content reduced to 1.10
percent, .[.being heat-treated.]., .[.wherein.]. .Iadd.of which
.Iaddend.the samples Nos. 6I to 6K are those .Iadd.which were
.Iaddend.treated according to the method of the present invention,
while the samples Nos. 6L to 6N are those treated according to
.Iadd.a .Iaddend.conventional method. The comparison of both groups
shows clearly the .[.quite.]. .Iadd.substantially .Iaddend.same
tendency with respect to the toughness at low temperature and the
workability of steel as is seen .[.at.]. .Iadd.in the comparison of
the samples Nos. 6C to 6G with No. 6H. The samples Nos. 6O and 6P
are steels, which contain Cu, and show that the high toughness at
low temperature can be obtained, even though the Mn content is
reduced to about 0.5 percent.Iadd., .Iaddend.if the steel is
treated according to the method of the present invention (for
instance, No. 6O). .[.At last.]. .Iadd.Finally.Iaddend., the
samples Nos. 6Q and 6R are steels, wherein Nb is added. In this
case too, an excellent toughness at low temperature can be imparted
to steel, if it is heat-treated according to the method of the
present invention (for instance No. 6Q).
As above mentioned, in the steels subjected to the heat treatment
of the present invention the toughness at low temperature is
remarkably improved and further the workability is .[.elevated.].
.Iadd.increased.Iaddend., as the yield stress is reduced, that is,
the yield ratio is lowered, while there is seen no change in the
tensile strength. Usually, in .[.the said.]. .Iadd.such
.Iaddend.steel.Iadd.s .Iaddend.which contain.[.s.]. a relatively
large amount of Mn, exceeding 1.0 percent and .[.is further.].
have, .Iadd.moreover, a .Iaddend.high .[.in the.]. Mo content,
cementite remains .[.till.]. .Iadd.up .Iaddend.to the high
temperature side .[.at the time of.]. .Iadd.during
.Iaddend.tempering, whereby the toughness is impaired. .[.In this
case, if.]. .Iadd.If .Iaddend.the tempering is .Iadd.therefore
.Iaddend.carried out at a high temperature in order to prevent the
above-mentioned phenomenon, the temper-formed austenite becomes
unstable.[.,.]. on cooling.Iadd., .Iaddend.resulting in a
deterioration of the toughness. .[.thereby.].. However, if the
steel is treated according to the method of the present invention,
austenite is precipitated .Iadd.in .Iaddend.very fine .Iadd.form
.Iaddend.and dispersedly in the steel and.Iadd., .Iaddend.in
addition thereto.Iadd., .Iaddend.the structure is very stable,
whereby an excellent toughness at low temperature can be obtained.
Further, .[.as reasons of improving the toughness of steel there
can be enumerated the following facts that.]. by the heat treatment
of the present invention.Iadd., .Iaddend.the tempered structure
becomes fine and the ferrite matrix .[.becomes a.]. .Iadd.is
rendered .Iaddend.pure .[.one.]. as a result of the tempering
thereof being well progressed. .Iadd.There are reasons for the
improvement of the toughness of the steels. .Iaddend.
In the following the structures of steels heat-treated according to
the present invention shall be explained in reference to the
attached figures (photograph). The samples and the treating methods
applied correspond to the above-mentioned samples Nos. 6E and 6H.
All figures show microphotographs of 4,500 magnifications.
.[.respectively.].. FIG. 2 shows a sample subjected to the
following heat treatment: a heating to 800.degree.C. for 1 hour
with a sequent air cooling therefrom.[.,.]..Iadd..
.Iaddend..[.wherein it.]. .Iadd.It .Iaddend.is .[.evidently seen.].
.Iadd.clearly seen .Iaddend.that the structure consists of
martensite and partly bainite. FIG. 3 is a photograph showing a
structure obtained by further subjecting the steel having the
structure as shown in FIG. 2 to the L-treatment of heating to
560.degree.C. for 1 hour and a sequent water cooling. From this
photograph it is clear that as a result of the L-treatment there is
produced a structure, wherein .[.a.]. martensite transformed from
precipitated .Iadd.or revertedly formed .Iaddend.austenite enriched
in C, Ni, Mn and N and precipitated finely in an insular form at an
old martensite subgrain boundary.Iadd., .Iaddend.is equilibrated
with ferrite, .Iadd.thus .Iaddend.forming a mixed structure of
them. The most important feature of the present invention lies just
in producing the above-mentioned structure. When the steel having
the structure as above mentioned is further subjected to the
T-treatment of heating the steel to 600.degree.C. for 1 hour with a
sequent water cooling, there is dispersedly precipitated .Iadd.or
formed .Iaddend.an ultrafine austenite in the tempered martensite,
as shown in FIG. 4.
This will be more clearly observed, when compared with the
structure of the reference sample shown in FIG. 5. .[.That is,.].
FIG. 5 .Iadd.thus .Iaddend.shows a structure of the steel treated
according to a conventional method, wherein the Q-treated steel of
FIG. 2 was directly subjected to the T-treatment at 600.degree.C.,
resulting in the production of a coarse.Iadd.ly
.Iaddend.precipitated .Iadd.or formed .Iaddend.austenite.
EXAMPLE 2
In table 2 there are shown the heat-treating methods .[.of.].
.Iadd.for .Iaddend.9% Ni-containing hot-rolled steel plates and
.Iadd.the .Iaddend.mechanical properties obtained thereby, wherein
the sample No. 9B is a steel treated according to a conventional
method, that is, .Iadd.the steel is .Iaddend.not subjected to the
L-treatment. From the comparison with the sample 9A of the present
invention it is clearly seen that the sample No. 9B .[.is.].
.Iadd.has a .Iaddend.far lower .[.in the.]. toughness at low
temperature than the sample No. 9A and also in .[.the.].
.Iadd.respect of .Iaddend.workability .Iadd.is .Iaddend.inferior to
the latter, as is shown by a higher yield ratio. Further, from FIG.
6 .[.showing.]. .Iadd.which shows .Iaddend.the relations between
impact value and tempering temperature .[.on.]. .Iadd.of
.Iaddend.the steel .[.shown by the.]. .Iadd.of .Iaddend.sample No.
9B, as compared with the steel treated according to the method of
the present invention .Iadd.(see black triangle).Iaddend., it is
seen that in the case of the reference steel (shown by a mark) the
range of proper T-treatment, that is, the range of tempering
temperature capable of obtaining high impact value is very narrow,
while in the case of the steel of the present invention the said
range is far wider, indicating that an excellent toughness can be
obtained in .[.the.]. .Iadd.a .Iaddend.wide range of tempering
temperature.
TABLE 2
__________________________________________________________________________
9%-Ni SERIES STEELS Chemical composition (wt. percent) Heat
treatment Plate thick- Steel Sol. Other ness. Nos. C Si Mn Ni Mo Al
element mm. Q L T
__________________________________________________________________________
9 A 0.04 0.25 0.43 0.05 -- 0.01 Balance Fe 13 800.degree.
C..times.60 mm. 670.degree. C..times.60 mm. 575.degree. C..times.
60 mm. W 9 B.sup.1 0.04 0.25 0.43 0.06 -- 0.01 Balance Fe 13
800.degree. C.times.60 mm.
__________________________________________________________________________
PQ Mechanical property Elongation Total Uniform elonga- elonga-
Steel .sigma. Y, .sigma.B, Y.R. tion, tion, vE-.sub..fourthroo
t..sub..degree. C. No. kg/mm.sup.2 kg./mm.sup.2 (.sigma. Y/.sigma.
B) percent percent .Iadd.kg.m/cm.sup. 2
__________________________________________________________________________
.Iaddend. -9A 63.2 73.1 0.87 30.0 13.4 30.5 9B.sup.1 70.2 75.3 0.93
24.4 10.5 7.9
__________________________________________________________________________
.sup.1 see Table 1 .Iadd.Remarks: PQ is pressure quench .Iadd.Other
signs are of the same meaning as in Table 1
The structures of steels subjected to various heat-treating methods
in the present example are .[.as.]. shown by microphotograph of
4,500 magnifications in FIGS. 7 to 10. .[.respectively.].. FIG. 7
is a microphotograph showing the struccture obtained by the
Q-treatment. From this photograph it is seen that the structure
.[.of.]. .Iadd.in .Iaddend.this case consists of a mixed structure
of martensite and partly bainite. FIG. 8 shows the structure
obtained by subjecting the steel having the structure shown in FIG.
7 to the L-treatment.[., wherein.]..Iadd.. .Iaddend.It is clearly
seen that fine martensite in the insular form is precipitated
.Iadd.or formed .Iaddend.in the ferrite matrix. When further
subjecting the sample of FIG. 8 to the T-treatment, there can be
obtained a structure .Iadd.as .Iaddend.shown by the photograph in
FIG. 9, wherein the tempered martensite is formed in the ferrite
matrix, where the tempering made progress, in said tempered
martensite ultra fine austenite being precipitated .Iadd.or
formed.Iaddend.. For the purpose of comparison there is shown in
FIG. 10 the final structure of sample No. 9B, which was not
subjected to the L-treatment. From this figure it is quite evident
that the temper formed .Iadd.or reverted .Iaddend.austenite has a
coarse structure, as compared with the structure shown in FIG.
9.
TABLE 3
__________________________________________________________________________
3%-Ni SERIES STEELS Chemical composition (wt. percent) Plate thick-
Heat treatment Steel Sol. Other ness, No. C Si Mn Ni Mo Al element
mm. Q L T
__________________________________________________________________________
3 A 0.10 0.24 0.69 3.03 0.30 Balance 11 900.degree.C..times.60 mm.
720.degree.C..times.00 mm. 500.degree.C..times.60 mm. WQ Fe. 3 B
0.10 0.24 0.69 3.03 0.36 do. 11 do. do. 550.degree.C..times.60 mm.
WQ 3 C 0.10 0.24 0.69 3.03 0.36 do. 11 do. do.
600.degree.C..times.60 mm. WQ 3 D.sup.1 0.10 0.24 0.69 3.03 0.36
do. 11 900.degree.C..times.00 mm. 500.degree.C..times.60 mm. WQ 3
E.sup.1 0.10 0.24 0.69 3.03 0.36 do. 11 do. 600.degree.C..times.60
mm. WQ 3 F 0.045 0.21 4.45 2.95 0.21 0.015 do. 11
800.degree.C..times.00 mm. 670.degree.C..times.60 mm. do. 3 G 0.015
0.21 4.45 2.95 0.21 0.015 do. 11 do. 700.degree.C..times.60 mm. do.
3 H.sup. 1 0.015 0.21 4.45 2.95 0.21 0.015 do. 11 do. do.
__________________________________________________________________________
Mechanical property Steel VTrs No. (.degree.C.) 11v 3 A -100 205 3
B -175 195 3 C -165 181 3 D.sup.1 -160 249 3 E.sup.1 -160 297 3 F
.sup.2 11.0 253 3 G .sup.2 15.6 260 3 H.sup.1 .sup.2 8.1 235
__________________________________________________________________________
.sup.1 See Table 1 .sup.2 vE-.sub.196.sub..degree. C. (kg. m./cm.).
Remarks: vTrs (.degree. C.) is V-notch Charpy 50% ductile
transition temperature. Other signs are of the same meaning as FIG.
1.
EXAMPLE 3
In Table 3 there are shown mechanical properties, particularly the
toughness and strength, of about 3.0% Ni-containing hot-rolled
steel plates manufactured by a conventional method, as subjected to
the Q-treatment and the T-treatment with or without the
L-treatment.
The samples Nos. 3A and 3C and Nos. 3F and 3G are the steels
treated according to the method of the present invention, including
the L-treatment, while the samples Nos. 3D, 3E and 3H are those
treated .[.to.]. .Iadd.by .Iaddend.a conventional method, wherein
the L-treatment is not included. From the comparison of both groups
it is clear that the steels of the present invention are far
superior in the toughness .[.to.]. .Iadd.as compared to that of
.Iaddend.conventional steels. .[.That is,.]. .Iadd.Thus,
.Iaddend.in the steels treated according to the method of the
present invention there is produced a very fine tempered structure,
wherein cementite is finely precipitated in islands of the tempered
martensite. Further, as the tempering of the ferrite matrix .[.is
made.]. .Iadd.makes .Iaddend.progress and there .[.are.]. .Iadd.is
.Iaddend.produced pure ferrite of fine grains which does not
contain cementite, a structure having an excellent toughness can be
obtained. FIG. 11 is a micro-photograph of 4,500 magnifications of
the final structure of the sample No. 3A, from which the
above-mentioned fact is .[.manifested to be true.].
.Iadd.apparent.Iaddend.. FIG. 12 is also a microphotograph of the
final structure of the sample No. 3D which was not treated
according to the method of the present invention, showing that a
coarse cementite is being extensively precipitated, which
establishe.[.d.]..Iadd.s .Iaddend.that the steel treated according
to the method of the present invention is superior to the
conventional steel.
As is above explained, .[.the.]. steel.Iadd., .Iaddend.heat-treated
according to the method of the present invention.Iadd.,
.Iaddend.has an excellent toughness at low temperature without
.[.being attended with a.]. reduction of the strength, .Iadd.and
.Iaddend.can be easily produced, because the optimum tempering
temperature extends over a wide range and further .Iadd.the steel
.Iaddend.can be used for various purposes, as the workability at
normal temperature is strikingly improved. However, the present
invention is not limited to the examples above-mentioned, but may
be modified variously within the scope of the objects of the
present invention.
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