Note: Descriptions are shown in the official language in which they were submitted.
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Dual Phase Steel with Improved Properties
BACKGROUND
[0001] It is desirable to produce steels with high strength and good
formability
characteristics. The present invention relates to steel compositions and
processing
methods for production of steel using thermal processing techniques such that
the
resulting steel exhibits high strength and/or cold formability.
SUMMARY
[0002] The present steel is produced using a composition and a modified
thermal process
that together produces a resulting microstructure consisting of generally
ferrite
and a second phase generally comprising martensite and bainite (among other
constituents). To achieve such a microstructure. the composition includes
certain
alloying additions and the thermal process includes a hot-dip
galvanizing/galvannealing (HDG) or other thermal process with certain process
modification.
BRIEF DESCRIPTION OF THE FIGURES
[0003] The accompanying figures, which are incorporated in and constitute a
part of this
specification, illustrate embodiments, and together with the general
description
given above, and the detailed description of the embodiments given below,
serve
to explain the principles of the present disclosure.
[0004] FIGURE 1 depicts a schematic view of a HDG temperature profile with
a
quenching step performed prior to galvanizing/gal vannealing.
[0005] FIGURE 2 depicts the HDG temperature profile of FIGURE 1, with the
average
cooling rate of the HDG temperature profile shown in phantom.
[0006] FIGURE 3 depicts a schematic view of an alternative HDG temperature
profile
with a quenching step performed after galvanizing/galvannealing.
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DETAILED DESCRIPTION
[0007] FIG. 1 shows a schematic representation of a combination of a
typical hot-dip
galvanizing thermal profile and a modified hot-dip galvanizing thermal
profile.
The modified thermal cycle is used to achieve high strength and good
formability
in a dual phase steel sheet (described in greater detail below). In a steel
sheet used
with the two thermal cycles shown in FIG. 1, the steel sheet generally
comprises
two phases after the thermal cycles ¨ a first phase of predominantly ferrite
and a
second phase. It should be understood that the term "second phase" used herein
is
generally used to refer to a phase generally comprising predominately
martensite
with some bainite. However, it should also be understood that such a second
phase may also include any one or more of cementite and/or residual austenite.
Additionally, it should be understood that while FIG. 1 is shown in connection
with hot-dip galvanizing, in other embodiments a galvannealing or other hot-
dip
coating process can be used. In still other embodiments, hot-dip coating
processes
are omitted entirely and the steel sheet is merely subjected to the thermal
profile
as shown.
[0008] The solid line in FIG. 1 shows a schematic view of the typical hot-
dip galvanizing
or galvannealing thermal profile (10). As can be seen, the typical thermal
profile
(10) involves heating the steel sheet to a peak metal temperature (12) and
optionally holding the steel sheet at the peak metal temperature (12) for a
first
predetermined period of time. In the present example, the peak metal
temperature
(12) is at least above the austenite transformation temperature (Al) (e.g.,
dual
phase austenite + ferrite region). Thus, at the peak metal temperature (12) at
least
a portion (by volume) of the steel will be transformed to a combination of
austenite and ferrite. Although FIG. 1 shows that peak metal temperature as
being
solely above A1, it should be understood that in some embodiments the peak
metal temperature may also include temperatures above the temperature at which
ferrite completely transforms to austenite (A3) (e.g., the single phase,
austenite
region).
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[0009] As stated above, in the typical thermal profile (10) the steel sheet
is held at the
peak metal temperature (12) for a first predetermined amount of time. It
should be
understood that the particular amount of time that the steel sheet is held at
the
peak metal temperature (12) may be varied by a number of factors such as the
particular chemistry of the steel sheet, or the desired volumetric quantity of
the
second phase in the steel sheet at the conclusion of the thermal cycle.
Additionally, in some circumstances the time held at the peak metal
temperature
(12) may be reduced to zero or near zero. In circumstances where the hold time
is
reduced, the peak metal temperature can be increased to compensate for such a
reduction.
[0010] Once the first predetermined period of time has elapsed, the typical
thermal
profile (10) involves rapidly cooling the steel sheet to an intermediate
temperature
(14). The steel sheet is then held at the intermediate temperature (14) for a
second
predetermined period of time. Generally, the steel sheet is held at the
intermediate
temperature (14) for a sufficient amount of time to permit the steel sheet to
reach
a temperature that is near the temperature of the zinc bath.
[0011] Still referring to the typical thermal profile (10), the steel sheet
is next inserted
into a liquid zinc galvanizing tub or galvannealing apparatus. During this
stage,
the temperature of the steel sheet is slightly reduced to a bath temperature
(16)
that is below the intermediate temperature (14). The bath temperature (16) is
generally below the intermediate temperature (14) to avoid dross formation
upon
entry of the steel sheet into the liquid zinc.
[0012] The steel sheet remains at the bath temperature (16) for the
duration of the
galvanizing. Where galvannealing is used, the steel sheet is removed from the
bath at some period of time and then elevated to an annealing temperature. The
particular temperature of the bath temperature (16) is at least above the
melting
point of zinc (e.g., 419 C, 787 F). However, it should be understood that in
some examples the bath temperature (16) may be even higher depending on the
particular configuration of the galvanizing bath or galvannealing apparatus.
It
should be also understood that in circumstances where the bath temperature
(16)
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is higher relative to the melting point of zinc, the intermediate temperature
(14)
may remain the same as shown, be correspondingly raised, or even lowered.
[0013] At the conclusion of the galvanizing or galvanealing process, the
steel sheet is
cooled below the martensite start temperature (Ms), thereby transforming at
least
some austenite into martensite. Of course, as described above, other
constituents
may form such as bainite, pearlite, or retained austenite. These constituents,
along
with the formation of martensite, form what is collectively described herein
as the
second phase. As described above, although the second phase may contain one or
more of martensite, bainite, pearlite and/or retained austenite, it should be
understood that the second phase is generally characterized by formation of
predominately martensite.
[0014] In some instances, modification to the typical thermal profile (10)
described
above is desirable. For example, because of the galvanizing or galvannealing
step
in the typical thermal profile (10), the average cooling rate from the peak
metal
temperature (12) to the martensite start temperature (Ms) may be insufficient
to
form a desirable volumetric quantity of martensite ¨ instead folining non-
martensitic transformation products (e.g., bainite, cementite, pearlite,
and/or etc.).
This may be the case regardless of how quickly the steel sheet is cooled after
galvanizing or galvannealing. To account for this relatively slow average
cooling
rate, conventional dual phase steels used in such a process often includes
high
alloy content to increase hardenability and thereby avoid formation of non-
martensitic transformation products. However, relatively high alloying
additions
may be undesirable due to increased cost and reduced mechanical properties.
Thus, it can be desirable to modify the typical thermal profile (10) described
above to maintain a desired amount of martensite in dual phase steels without
high alloying additions. Further modifications described below, such as
reheating
from below the martensite start temperature (Ms) to the intermediate
temperature
(14), may additionally be desirable to improve mechanical properties such as
hole
expansion ratio (HER) or yield strength (regardless of the particular amount
of
alloying additions).
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[0015] In the present embodiments of the modified thermal profile,
improvements to the
mechanical properties were more significant than expected, especially when
considering the relatively short tempering time (e.g., duration of time during
which the steel sheet is exposed to the zinc bath).
[0016] As shown in FIG. 1, the typical thermal profile (10) described above
can be
modified to include a quench step (18) prior to the galvanizing or
galvannnealing
step described above. As can be seen, this alternative procedure is generally
identical to the procedure described above with the exception of the portion
of the
procedure related to the intermediate temperature (14). In particular, instead
of
quenching the steel sheet from the peak metal temperature (12) to the
intermediate
temperature (14), the steel sheet is quenched from the peak metal temperature
(12) to a quench temperature (20). It should be understood that the cooling
rate
from the peak metal temperature (12) to the quench temperature (20) is
generally
high enough to transform at least some of the austenite formed at the peak
metal
temperature (12) to martensite. In other words, the cooling rate is rapid
enough to
transform austenite to martensite instead of other non-martensitic
transformation
products such as ferrite, pearlite, or bainite which form at relatively lower
cooling
rates.
[0017] In the present example, the quench temperature is below the
martensite start
temperature (MO. The difference between the quench temperature (20) and the
martensite start temperature (Ms) can vary depending on the individual
composition of the steel sheet being used. However, in many embodiments the
difference between quench temperature (20) and M, is sufficiently great to
form a
predominately martensitic second phase.
[0018] Once the quench temperature (20) is reached, the temperature of the
steel sheet is
maintained at the quench temperature for a predetermined quench time. Because
formation of martensite is nearly instantaneous, the particular amount of time
during which the steel sheet is at the quench temperature is generally
insignificant.
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[0019] After quenching to the quench temperature (20). the steel sheet is
reheated to the
intermediate temperature (14) or to another temperature at or near the bath
temperature (16). In the present example, reheating is relatively quick and
may be
performed using various methods such as induction heating, torch heating,
and/or
other methods known in the art. Once reheated, the steel sheet is inserted
into a
zinc bath. In the zinc bath, the steel sheet will reach the bath temperature
(16), as
described above, where the steel sheet will remain for the remainder of the
galvanizing. The particular amount of time during which the steel sheet is in
the
zinc bath is largely determined by the galvanizing/galvannealing process.
However, it should be understood that during this time, the martensite is
tempered
to thereby improve the mechanical properties of the steel sheet. Where a
galvannealing process is used, the steel sheet may be heated to an annealing
temperature after removal from the bath.
[0020] Although the reheating step is described herein as being in
connection with a
coating step, such as galvanizing or galvannealing, it should be understood
that no
such limitation is intended. For instance, in some examples the reheating step
may
merely be performed and then the process may proceed as described below. In
such examples, the steel sheet is held at the intermediate temperature (14) or
the
bath temperature (16) despite not actually being subjected to a galvanizing or
galvannealing treatment. Additionally, in some examples the steel sheet may be
held at a lower temperature (e.g., 400 C) relative to the bath temperature
(16)
because heating the steel sheet to the melting point of zinc is not necessary
without application of zinc. The steel sheet may be held at such a temperature
for
any suitable time as will be apparent to those of ordinary skill in the art in
view of
the teachings herein.
[0021] Once the galvanizing, galvannealing, or other similar thermal
process is
completed, the steel sheet is cooled to room temperature, as similarly
described
above. Accordingly, in the present example, the steel sheet is first heated to
a
peak metal temperature (12) to form austenite and optionally ferrite. Next the
steel sheet is cooled from the peak metal temperature (12) to the quench
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temperature (20) to form martensite or other constituents of the second phase.
After quenching, the steel sheet is reheated to approximately the zinc bath
temperature for galvanizing and optionally galvannealing. Finally, the steel
sheet
is cooled to ambient temperature.
[0022] FIG. 2 shows a comparison of the average cooling rate (30) of the
typical thermal
profile (10) versus the average cooling rate (32) of the typical thermal
profile (10)
modified to include the quench step (18). As can be seen, the quench step (18)
substantially reduces the average cooling rate of the typical thermal profile
(10).
In examples where the method described herein is used in a continuous
galvanizing/galvannealing line, average cooling rate may depend at least
partially
on the feed speed of the galvanizing/galvannealing line. For instance, where
feed
speeds of about 30 meters per minute are used, the average cooling rate using
the
typical thermal profile (10) is about 17 C per second, while the average
cooling
rate using the modifications described herein is about 48 C per second. In
examples where feed speeds of about 91 meters per minute are used, the average
cooling rate using the typical thermal profile (10) is about 6 C per second,
while
the average cooling rate using the modifications described herein is about 16
C
per second. In yet other examples where feed speeds of about 120 meters per
minute are used, the average cooling rate using the typical thermal profile
(10) is
about 4 C per second, while the average cooling rate using the modifications
described herein is about 12 C per second.
[0023] Regardless of the particular cooling rate achieved, it should be
understood that
improved mechanical properties of the steel sheet can be achieved by reheating
the steel sheet as described above. These improvements can be achieved whether
the steel sheet includes conventional dual-phase alloy compositions or
compositions with relatively low alloying elements described herein.
[0024] In embodiments where reduced cooling rates are achieved, it should
be
understood that because of the reduction in the average cooling rate,
martensite is
more readily formed when the quench step (18) is added to the typical thermal
profile (10). Since the conditions increase the propensity to form martensite,
less
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alloying elements are required in the steel sheet. Thus, when the quench step
(18)
is applied to the typical thermal profile (10) described above, dual phase
steel can
be galvanized or galvannealed with substantially less alloying elements.
Despite
having less alloying elements, the steel sheet can have similar post heat
treatment
martensite content as conventional dual phase steels treated using only the
typical
thermal profile (10).
[0025] It should be understood that in some examples it may be desirable to
modify the
typical thermal profile (10) such that the quench step (18) is performed after
galvanizing/galvannealing instead of before. One such example can be seen in
FIG. 3. In FIG. 3, the quench step (18) may be performed as similarly
described
above with a rapid cooling of the steel sheet below the martensite start
temperature (MO. When the quench step (18) is performed after galvanizing or
galvannealing as shown in FIG. 3, the average cooling rate from the peak metal
temperature (12) to the intermediate temperature (14) or bath temperature (16)
is
similar to the average cooling rate (30) for the typical thermal profile (10)
shown
in FIG. 2. Because this is a relatively low cooling rate, it should be
understood
that martensite formation will be reduced as similarly encountered in the
typical
thermal profile (10). With less martensite formation, higher alloying elements
may be required to achieve desirable levels of martensite. Thus, applying the
quench step (18) after galvanizing or galvannealing will not achieve cost
savings
associated with reduced alloying content. However, applying the quench step
(18)
after galvanizing or galvannealing will still nonetheless promote improved
mechanical properties such as hole expansion ratio (HER) and yield strength.
In
some examples, these improvements to the mechanical properties of the steel
sheet can be comparable to those improvements achieved through applying the
quench step (18) prior to galvanizing or galvannealing.
[0026] In some variations of the process where the quench step (18) is
applied after
galvanizing or galvannealing, a tempering step (40) may also be performed,
where the steel sheet is heated to a predetermined temperature above or below
the
martensite start temperature (M,) for a predetermined period of time after the
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quench step (18). When such a tempering step is used. the average cooling rate
is
also similar to the average cooling rate (30) for the typical thermal profile
(10)
shown in FIG. 2. Thus, high alloy content will still be required to form a
predominantly martensitic second phase. However, such a tempering step further
improves mechanical properties such as hole expansion ratio (HER) and yield
strength.
[0027] The steel sheet may include various alloying elements typically
present in
conventional dual phase steels. For instance, in some embodiments, carbon
provides increased strength. For instance, increasing carbon concentration
generally lowers the Ms temperature, lowers transformation temperatures for
other
non-martensitic constituents (e.g., bainite, ferrite, pearlite), and increases
the time
required for non-martensitic products to form. Additionally, increased carbon
concentrations may improve the hardenability of the material thus retaining
formation of non-martensitic constituents near the core of the material where
cooling rates may be locally depressed. However, it should be understood that
carbon additions may be limited as significant carbon concentrations can lead
to
detrimental effects on weldability. Furthermore, in greater concentrations
carbon
can have a detrimental effect of formability. Therefore, the carbon content is
generally kept around 0.067- 0.14% by weight.
[0028] In some embodiments manganese provides increased strength by
lowering
transformation temperatures of other non-martensitic constituents and
increasing
the amount of martensite. Manganese can further improve the propensity of the
steel sheet to form martensite by increasing hardenability. Manganese can also
increase strength through solid solution strengthening. However, the presence
of
manganese in large concentrations can degrade formability. Therefore the
manganese content is generally present in the concentration of about 1.65-2.9%
by weight.
[0029] In some embodiments aluminum additions are made to provide
deoxidization.
However, aluminum additions beyond certain levels can lead to formability
being
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degraded. Accordingly, aluminum is generally present in the concentration of
about 0.015-0.07% by weight.
MON In some embodiments silicon can be added to promote a dual phase
structure
consisting of predominately ferrite and martensite. However, when silicon is
increased beyond certain concentrations, zinc will not adhere as effectively
to the
steel sheet. Accordingly, silicon is generally present in the concentration of
about
0.1-0.25% by weight.
[0031] In some embodiments niobium is added to refine ferrite grains. Such
grain
refinement is desirable to improve formability and improve weld quality.
However, if niobium concentrations exceed a certain amount, formability of the
steel sheet will degrade. Accordingly, niobium is generally present in the
concentration of about 0-0.045% by weight. Alternatively, in some examples
niobium is present in the concentration of about 0.015-0.045% by weight.
[0032] In some embodiments vanadium is added to increase hardenability
and/or refine
ferrite grains. When added, vanadium is generally included in a concentration
less
than or equal to 0.05% by weight.
[0033] In some examples chromium is added to improve formability and weld
quality.
However, chromium additions exceeding certain concentrations will result in
low
quality surface properties. Accordingly, chromium may be included in the
concentration of about 0-0.67%. or 0.2-0.67% by weight.
[0034] In other embodiments molybdenum may be used to increase
hardenability. When
molybdenum is used, molybdenum can be included in a concentration of about
0.08-0.45% by weight. In other embodiments the lower limit concentration of
molybdenum is reduced further, or even eliminated entirely.
[0035] In some embodiments titanium and boron are added to increase
strength. It should
be understood that in some embodiments titanium and boron may be used
together, separately in lieu of the other, or neither element may be used.
When
titanium is used, titanium is present in the concentration of about 0.01-0.03%
by
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weight. When boron is used, boron is present in the concentration of about
0.0007-0.0013% by weight.
[0036] In embodiments where titanium and boron are added together, titanium
is
generally present in suitable concentrations to substantially prevent boron
from
forming nitrides. Thus, titanium may be included to combine with nitrogen
prior
to the nitrogen combining with boron. In some circumstances titanium is
included
in concentrations of about 3.43 times the weight percent of nitrogen. When
included in this concentration, titanium generally combines with nitrogen,
thereby
preventing boron from forming nitrides.
[0037] In other embodiments, variations in the concentrations of elements
and the
particular elements selected may be made. Of course, where such variations are
made, it should be understood that such variations may have a desirable or
undesirable effect on the steel sheet microstructure and/or mechanical
properties
in accordance with the properties described above for each given alloying
addition.
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EXAMPLE 1
[0038] Embodiments of the steel sheet were made with the compositions set
forth in
Table 1 below.
12
Table 1 Chemical compositions in weight %.
Cast C Mn Al Si Nb V Cr Mo
Ti
Cod
0
e Min Max Min Max Min Max Min Max Min Max Min Max Min Max Min Max Min Max Min
Max r.)
A 0.08 0.10 1.70 1.90 0.03 0.06 0.15 0.25 0.015 0.025
0.010 0.20 0.30 - 0.02 0.01 0.03 0.001
B 0.067 0.08 1.65 1.82 0.02 0.07 0.15 0.25 0.001 0.030 0.050 -
- 0.16 0.20 0.01 0.02 0.001
C 0.10 0.12 2.10 2.30 0.03 0.06 0.15 0.25 0.003
0.010 0.20 0.30 0.25 0.35 0.003 0.001
D 0.10 0.12 1.75 1.90 0.02 0.07 0.15 0.25 0.035 0.045
0.008 0.20 0.30 0.15 0.20 0.01 0.020 0.001
E 0.11 0.13 2.40 2.70 0.03 0.06 0.15 0.25 0.004
0.008 0.30 0.40 0.35 0.45 0.005 0.0007
F 0.08 0.10 2.00 2.20 0.03 0.07 0.40 0.50 0.040 0.060
0.008 0.20 0.30 0.30 0.40 0.008 0.001
G 0.09 0.10 2.25 2.42 0.015 0.07 0.10 0.20 0.035 0.045
0.008 0.57 0.67 0.08 0.12 0.030 0.0007 0.0013
H 0.12 0.14 2.70 2.90 0.03 0.06 0.15 0.25 0.004 -
0.008 0.30 0.40 0.35 0.45 0.005 0.0007
to
0.
I 0.11 0.13 2.45 2.60 0.015 0.05 0.42 0.58 0.035 0.045
0.020 0.57 0.63 - 0.05 0.015 0.025 0.0012 0.002
to
0
1-`
C7)
13
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EXAMPLE 2
[0039] Embodiments of the steel sheet made with the compositions set forth
above in
Table 1 were subjected to mechanical testing. Mechanical properties for a
selected
number of the compositions set forth in Table I are set forth below in Table
2.
14
Table 2 Mechanical properties for selected compositions of Table 1.
Example
r.)
Alloy Quench Temperature YPE YS UTS TE HER
of Cast
Note
No. ( C) (%) (MPa) (MPa) (%) (%)
Code
I
Comparative
Not applicable 0 420 780 15 20
Example
4 250 1.4 690 780 15 60
Comparative
Not applicable 0 650 980 11 20
Example
6 250 1 840 980 13 50
Comparative
Not applicable 0 800 1180 8
Example
9 250 2.4 1120 1165 10 55
2
0
0
CID
oe
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EXAMPLE 3
[0040] Embodiments of the steel sheet were made with the compositions set
forth in Table 3
below. The particular compositions shown in Table 3 are based on the
compositional
ranges set forth in Table 1.
16
Table 3 Chemical compositions in weight %.
Alloy Example of Cast
0
Al B C Ca Cr Cu Mn Mo N Nb Ni
P S Si Sn Ti V
No. Code
r.)
o
<0.000 <0.00
<1100 0.000 <0.00 <0.00 <0.00 0.000 <0.00 <0.00 <0.00
1 C w/o Mo 0.042 0 0005 0 094 0.25
2.19 0.19 cr,
3 3 3 4 3 3 3
4 3 3 3 --...
1-,
000 < <0.000 <1100 Ø00 <0.00 0.000
<0.00 <0.00 <0.00 ...,
2 C 0.037 0.0004 0.093 0.25 2.27 0.3
0 0.003 0.18 tn
3 3 5 3 3
6
o
<0.000 <0.00 <0.00 0.001
<0.00 <0.00 0.000 <0.00 <0.00 ta
3
3 D w/o Mo 0.041 0.0004 0.1 0.25 1.86 0.042 0.2
0.015 3 3 2 3 3 . <0.000 <0.00 0.001 <0.00
<0.00 0.000 <0.00
4 D 0.039 0.0004 0.1 0.25 1.87 0.18
0.042 0.2 0.015
3 3 1 3 3
2 3 3
000 <0.00 <0.00 <0.00
<0.00 <0.00
F w/o 1\4o 0.046 0.0004 0.087 <0. 0.25 2.04 0.001
0.053 <0.00 0.000 0.43 <0.00
3 3 3 3 3
5 3 3 3
<0.000 <0.00
<0.00 <0.00 0.000 <0.00 <0.00 <0.00
6 F 0.044 0.0004 0.086 0.25
2.09 0.35 0.001 0.053 0.43
3 3 3 3
5 3 3 3
<0.000 <0.00 <0.00 0.000
<0.00 <0.00 0.000 <0.00 <0.00 <0.00
.61 2.24 0.04
0.14
3 3 3 4 3 3
5 3 3 3
<0.000 <0.00 o.000
<0.00 <0.00 o.000 <0.00 <0.00 <0.00
8 G 0.036 0.0013 0.091 0.61 2.26 0.096
0.043 0.15
3 3 4 3 3
4 3 3 3 0
<0.000 <0.00
<0.00 0.000 <0.00 <0.00 <0.00 0.000 <0.00 <0.00 <0.00 0
,..,
.35 2.76
0.19 .
3 3 3 6 3 3 3
4 3 3 3 .4
IV
<0.000 <0.00
0.000 <0.00 <0.00 <0.00 0.000 <0.00 <0.00 <0.00 4
...1
H 0.04 0.0005 0.13 0.34 2.72
0.4 0.19 0
3 3 8 3 3 3
4 3 3 3 np
<0.00 <0.00 <0.00 0.000 <0.00 <0.00 0.000 <0.00 <0.00 0
11 I w/o Cr 0.029 0.0025 0.12 0.0003
2.47 0.042 0.49 0.021 1-`
-4
3 3 3 8 3 3
4 3 3 0
<0.00 <0.00 0.001 <0.00 <0.00 0.000 <0.00
12 I 0.028 0.0026 0.12 0.0003 0.58
2.48 0.045 0.49 0.021 ,.
3 3 1 3 3 5 3 3 .4
n
i-i
cr
t...)
c,
c,
,
c...,
t.,.,
oe
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EXAMPLE 4
[0041] Embodiments of the steel sheet made with the compositions set forth
above in
Table 3 were subjected to mechanical testing. Mechanical properties for each
of the
compositions set forth in Table 3 are set forth below in Tables 4 through 15.
18
Table 4 Mechanical properties for alloy no. 1 of Table 3.
0
t...)
o
EUL
hole
Time at Time at Time at Unifor
cr,
Temper Temper Temper Stress 0.2%
Totaffil Hardne Expans --....
Alloy Temper Temper Temper IIY LYS YPE TITS
(M m ongatio ss ion Note
1¨,
ature 1 ature 2 .0)
...,
No. ature 1 ature 2 ature 3 OYS(
ature 3 S(MPa) (MPa) (%) Pa)
Elongat tn
( C) ( C) ( C) 0.5% MPa)ion(%) n
(%) (HRA) Ratio c...)
(s) (s) (s)
(MPa)
(%) o
ta
1 800 180 250 30 466 50 562 556
726 8 14 61
1 800 180 250 30 466 50 522 526
699 9 16 61
1 800 180 250 30 466 100 489 474
677 9 18 88
1 800 180 250 30 466 100 389 378
643 15 23 88
1 800 180 250 30 466 100 498 485
678 10 19 88
1 800 180 250 30 466 120 467 450
665 10 17 75
1 800 180 250 30 466 120 471 454
664 10 14 75
1 800 180 250 60 466 40 465 475
660 10 17 58 65
1 800 180 250 120 466 80 480 453
665 10 16 55 95 0
1 800 180 SKIP SKIP 466 50 392 384
649 14 22 55 Comparative 0
,..,
1 825 180 250 60 466 40 577 570
728 8 13 55 81 .4
IV
4
1 825 180 250 120 466 80 664 668
767 5 10 59 102. ...1
0
1 850 180 250 30 466 50 762 772
848 5 8 109 np
0
1-`
1 850 180 250 30 466 50 736 745
823 5 9 109 ,
0
1 850 180 250 30 466 100 763 768
834 5 8 102 .
,.
1 850 180 250 30 466 100 759 768
832 5 8 102 .4
1 850 180 250 30 466 120 725 731
805 5 8 110
1 850 180 250 30 466 120 735 742
809 4 8 - 110 . 1 850 180 250 60 466 40 868
870 915 5 9 62 91
1 850 180 250 120 466 80 819 823
859 4 7 62 96
n
i-i
CP
C..)
0
1¨,
0
-....
0
1¨,
Co4
Co4
CA)
00
19
Table 5 Mechanical properties for alloy no. 2 of Table 3.
0
t...)
EUL
o
hole
Sires
Harcin cr,
Tempera Time at Tempera Time at Tempera Time at UY
LYS 0.2% Uniform Expans --....
Allo YPE s ("& I ITS(M Pa)
Elongat. TotalEl ong ess
ture 1 Tempera ture 2 Tempera ture 3 Tempera
S(M (MPa OYS(1µ4 io ion Note ...,
(%) 0.5% at ion (%) (HRA y No. (oC) ture i(s)
( C) ture 2 (s) (DC) ture 3 (s) Pa)
Rati tn
) (MPa Pa) n(%)
)
o c...)
o
(%) ta
)
2 800 180 150 30 466 50 577 584 811 9
15 49
2 800 180 250 30 466 50 575 581 813 9
16 49
2 800 180 250 30 466 100 623 628 855 8
14 21
2 800 180 250 30 466 100 583 583 836 8
14 21
2 800 180 250 30 466 120 484 474 850 9
14 32
2 800 180 250 30 466 120 435 418 843 10
15 32
2 800 180 250 60 466 40 673 687 849 7
9 62 27
2 800 180 250 120 466 80 678 684 857 8
14 62 56
2 800 180 SKIP SKIP 466 50 469 457 843
10 16 24 Compara 0
2 800 180 SKIP SKIP 466 50 459 453 829
10 16 24 Compara 0
,..,
2 825 180 250 60 466 40 716 726 855 6
10 63 83 .4
IV
4
2 825 180 250 120 466 80 815 824 891 6
11 63 92 ...1
0
9 850 180 250 30 466 50 891 914 990 5
7 86 np
0
1-`
2 850 180 250 30 466 50 878 901 975 5
9 86 ,
0
2 850 180 250 30 466 100 845 864 938 4
7 106 .
,.
2 850 180 250 30 466 100 836 863 940 4
7 106 .4
2 850 180 250 30 466 120 843 866 943 4
7 93
2 850 180 250 30 466 , 120 , 828 , 845 931 , 4
, 8 93
2 850 180 250 60 466 40 977 971 0 969 973
1007 5 9 64 78
2 850 180 250 120 466 80 951 946 0 949 946
978 5 9 64 104
n
i-i
CP
C..)
0
1¨,
0
-....
0
1¨,
Co4
Co4
CA)
oe
Table 6 Mechanical properties for alloy no. 3 of Table 3.
0
t...)
EUL
o
hole
Allo
1¨,
cr,
1¨,
Tempera Time at Tempera Time at Tempera Time at UY LYS ypE
Sires 0.2%
I ITS(M
Uniform Hardu
TotalElong
ess Expans --...
No
...,
y
ture 1 'fempera ture 2 'fempera ture 3 Tempera S(M
(MPa (go 0.5% OYS(M pa) Elongatio
ation (%)
(HRA ion Note
tn . (oC) ture i(s) ( C) ture 2 (s) (DC) ture
3 (s) Pa) ) (MPa Pa) n(%)
)
Ratio
(%)
c...)
o
ta
)
3 800 180 150 30 466 50 606 606 764 9
15 51
3 800 180 250 30 466 50 595 595 756 10
15 51
3 800 180 250 30 466 100 626 628 765 9
13 53
3 800 180 250 30 466 100 609 609 752 8
12 53
3 800 180 250 30 466 120 625 625 766 9
12 43
3 800 180 250 30 466 120 593 595 746 9
13 43
3 800 180 250 60 466 40 619 612 1 613 612
760 10 16 60 52
3 800 180 250 120 466 80 622 616 1 616
618 745 10 17 59 52
3 800 180 SKIP SKIP 466 50 561 559 748
11 15 37 Compara 0
0
3 800 180 SKIP SKIP 466 50 579 578 758
11 15 37 Compara "
3 825 180 250 60 466 40 582 572 1 575 574
732 12 18 59 69 ,
IV
4
3 825 180 250 120 466 80 576 568 1 568
570 711 11 18 59 70 ...1
0
3 850 180 250 30 466 50 679.2 678.7 0.44 672 674 770
8 12 66
0
1-`
3 850 180 250 30 466 50
668.7 663 0.4 667 665 760 9 14 66 ,
3 850 180 250 30 466 100
669.2 651 1.47 658 658 744 9 14 67 g
,.
3 850 180 250 30 466 100 626.5 620.3 0.73 621 621 728
9 14 67 ,
3 850 180 250 30 466 120 681.9 655.6 1.93 656 657 739
9 13 85
3 850 180 250 30 466 , 120 , 654.1 637.9 ,
2.22 638 , 640 733 , 8 , 13 85
3 850 180 250 60 466 40 649 608 3 609 610
698 12 22 59 78
3 850 180 250 120 466 80 624 594 2 595
595 697 12 20 58 84
3 850 180 SKIP SKIP 466 50 580.2
577.4 0.7 580 580 706 12 18 89 Compara
3 850 180 SKIP SKIP 466 50 556 556 697
12 20 89 Compara
n
i-i
CP
C..)
0
1¨,
0
-....
0
1¨,
Co4
Co4
CA)
oe
21
(1 Table 7 Mechanical properties for
alloy no. 4 of Table 3.
I'.)
to
.....1
K.)
.....1 EU
Bole
0 LY L
Hardn
All Tempera Time at Tempera Time at Tempera
Time at UY 0.2% Uniform Expans
K.) S VP St
UTS(M . TotalElong ess
o oy ture 1 Tempera ture 2 Tempera ture 3
Tempera S(M num E OYS(M Pa) Elongatm atton (%) (HRA
Raiotnio Note
i-. No. (CC) ture 1 (s) CC) ture 2 (s) ( C) ture
3 (s) Pa) `Z (%) SS Pa) n(%)
co @
) (Vo)
I
0 0.5
to ....
I 4 SOO 180 250 30 466 50 - - 711 724
866 7 10 - 36
K.) 4 800 180 250 30 466 50 - 698 713
855 8 12 - 36
co 4 800 180 , 250 30 _ 466 100
- 721 734 860 6 7 - 63
-
4 SOO _ 180 250 30 466 100 - 717 , 728
857 5 7 - 63
4 800 180 250 30 466 120 - 713 722 863
8 12 - 43
4 800 180 250 30 466 120 - 702 707
845 , 9 12 - 43
_
4 800 180 250 60 466 , 40 _ _ -
705 706 854 8 14 59 34
-
4 800 , 180 250 120 466 80 - 755 765 877
7 12 62 53
4 800 _ 180 SKIP SKIP 466 50 _ - - 609
615 841 9 14 - 35 Compare
4 800 180 _ SKIP SKIP 466 50 - - 606 608
839 10 15 - 35 Cornpara
4 825 180 250 60 466 40 - 689 693 820
9 13 60 57
ry 4 825 180 250 120 466 80 - 679
679 819 9 15 63 69
4 850 180 250 ,_. 30 466 50 720.5 719
720 814 8 13 _ - 53
_ 4 850 180 ¨ 250 30 466 50 722 726 824
7 11 - 53
_
_ 4 850 180 250 30 466 100 705.5 701 704 705
799 8 12 - 62
. .
4 850 180 _ 250 30 466 100 710.5 708
708 710 804 7 10 - 62
4 850 180 250 30 , 466 120 720.8 710
710 796 8 12 94
4 850 180 250 30 466 120 , 689.6 689 690
779 8 12 - 94
4 850 180 250 60 466 _ 40 717 694 1 695 695
785 9 15 59 65
_
4 850 180 250 120 466 80 695 675 1 682 682 779 9 15 58 58
_
4 850 180 SKIP SKIP 466 _ 50 - -
626 628 775 10 16 63 Compare
-
4 850 180 SKIP SKIP 466 50 - - - 624
625 771 10 14 - 63 Compara
0
IV
l.0
-..1 Table 8 Mechanical properties
for alloy no. 5 of Table 3.
It.)
in.
-..1
0
IQ
0
i-, EU
Hole
co oI All Tempera Time at Tempera Time at Tempera Time at UY IN
'IT L UTS Uniform Hardn Expans
(M TotalElong ess
to oy ture 1 Tempera ture 2
Tempera -lure 3 Tempera S(M imp oh '" OYS(M pa) Elongatio ati
on eh) (HRA ion Note
iv! No. ( C) ture 1 (s) ( C) ture 2 (s) (CC)
ture 3 (a) Pa) v): `) ; Pa) n(%)
) Ratio
co
(%)
0.5
-
_
_ ..
_ _
800 180 250 30 _ 466 50 559.2 0.6 561 560
782 12 s 17 - -
_
.
_
_
5 800 180 250 30 466 50 579.7 580 580
803 11 16 - -
_
. _
_ 5 800 180 250 30 466 100 575.9 572 _ 571
803 11 17 - 28 .
_ 5 800 , 180 250 30 466 100 613 607 _
607 810 10 14 - 28 _
_
5 800 180 250 30 466 120 565.3 567 567
785 11 17 - 36
_
5 ' 800 - -
180 250 30 466 120 551.1 557 556 805
10 15 36 .
_ -
5 800 7 180 250 60 466 40 574 572 1 575
576 788 11 16 60 32
5 800 , 180 250 120 466 80 634 634 830
10 15 59 40
_
t..)" 5 800 180 SKIP SKIP 466 50 493
490 805 11 16 - 34 , Compare _
,
- .
5 800 - 180 SKIP SKIP 466 50 - 499 495
788 11 16 - 34 Compare
_
-
5 825 180 250 60 466 40 536 536 735
13 18 58 55
5 825 180 250 120 466 80 541 535 1 538 _
537 734 11 18 56 55
-
5 850 ' 180 250 30 466 50 650.7 628 628
755 11 17 51 _
_ _ _
_
5 850 ' 180 250 - 30 466 50 559.3 1.6 553 552
735 12 17 - Si
_
.
-
5 850 180 250 30 466 100 581.7 580 580
760 11 16 - 66 _
_
5 850 , 180 250 30 - 466 100 563 562 563
563 735 11 17 - 66 .
_
-
5 850 180 250 30 - 466 120 609.1 599 599
757 12 18 - 61 _
- _
5 850 180 250 30 466 120 - 590.4 _ 586 586
737 11 19 - 61
5 850 180 250 60 - 466 40 593 580 1 585
584 731 13 19 57 64
_
-
5 850 180 250 60 466 40 593 580 1 585 584 731 13 19 57 64 _
_
5 850 180 250 120 466 80 564 553 1 553 553 716 12 20 56 49
0
Table 9 Mechanical properlies for alloy no. 6 of Table 3.
I)
to
--.1
IV
--.1 -.-_
0 r EU _
Hole
All Tempera Time at Tempera Time at Tempera
Time at UY LY YP L 0.2% Uniform Expans
0 S E sire
UTS(M TotalElong eat
i-. oy lure 1 Tempera ture 2 Tempera
Cure 3 Tempera S(M nui, f% _E4 OYS(M pa)
Elongatio ion Note
anon (%) (HRA
co
i No. ( C) tura 1 (a) ( C) Cure 2 (a) ( C)
ture 3(s) Pa) .c).- `µ ' Pa) nCY0) Ratio
o /
) WO
to 0.5
tv 6 800 180 250 30 466 50 593 592
964 8 12 - 30
6 800 180 250 30 466 50 604 603 975 8
12 - 30
_ .
6 800 180 250 30 466 100 557 552 _ 995 8
12 - 24
_
_
6 800 180 250 30 466 100 554 548 991 8
11 - 24
_
6 800 , 180 250 30 466 120 551 547 972 8
14 - 23
. _ ..
_
6 800 180 250 30 466 120 559 556 983 8
13 - 23
6 800 180 250 60 466 40 793 791 1 793 798 997 8 13 67 23
_
6 800 180 250 120 466 80 741 739 0
739 739 987 _ 8 13 65 33
_
6 800 180 SKIP SKIP 466 50 598 613 1003
7 13 - 24 Compara
- -
.
iv 6 800 180 SKIP SKIP 466 50 602
618 1002 7 12 - 24 Compara
A - _
-
6 825 180 250 60 466 40 814 812 0 814 815 989 8 12 64 46
_ .
6 825 180 250 120 466 , 80 885 866 2 879 866 964 9 14 65 53
6 850 180 250 30 466 50 731.1 714 715
873 9 16 36
_
.
6 850 180 250 30 466 50 724.6 _ 718 725 725
874 10 16 - 36
6 850 180 250 30 466 100 685.6 _ 694 696
899 9 13 _ 50
_
.
6 850 180 250 30 , 466 100 693.8 693 702 703 899
8 14 - 50
_
.
6 850 180 250 30 466 120 720.6 706 707
892 9 16 - 43
_
,
_
6 850 180 250 30 466 120 715.3 _ _ 708 708
889 9 15 - 43
. .
6 850 : 180 - 250 60 466 40 792 _ 762 1
782 767 878 9 15 64 62
6 850 180 250 120 466 80 807 776 2 782 786
i
893 9 15 62 58
Cl Table 10 Mechanical properties
for alloy no. 7 of Table 3.
Iv
l0
.
=-.1
N.)
r1..
=-.1
_______________________________________________________________________________
___________________________ i
0 EU
Hole
Hardn
N.)All Tempera Time at Tempera Time at Tempera Time at UY LYS YP L
01%
UTS(M Uniform
TotalElong
ess
No. ( C) tore 1 (s)
( C) Expans
0 oy tore 1 Tempera tore 2 Tempera
tore 1 Tempera 5(M (MP E Stre OYS(M },a) Elongatio -
ion Note
1-.
asion (7e) (HRA
co lure 2 (s) ( C) ture 3 (s) Pa)
a) (%) ss P a) n(%) Ratio
I @
) (%)
iD 05
. -
I 7 800 180 250 30 466 50 688 697 929
, 8 12 - 36
n.) _ _ _ _
_
co 7 800 180 250 30 466 50 7 697 709
941 8 12 36
7 800 , 180 250 _ 30 466 100 _ 666
678 915 6 9 - 41
7 800 180 250 _ 30 -,_ 466 100
719 733 936 7 7 - ____ 41
7 800 180 --: 250 _ 30 _ 466
120 , 567 566 928 _ 8 11 _ - 32
_
_ _
7 800 180 250 30 466 120 563 563
918 8 11 - 32
7 800 180 , 250 60 466 40 655 653 0 637 638 919
9 13 64 32
_ _ _ _
-
-
7 800 180 250 120 466 80 797 790 _ _ _ _
_ 1 792 791 956 8 13 62 37
_ - -
7 800 180 SKIP SKIP 466 50 542
550 938 9 14 - 30 Compara
7 800 180 I SKIP _ SKIP 466 50 r -
553 562
950 8 11 30 Compara
NJ _ _ ¨
_
c.n 7 825 180 250 _ 60 _ 466 40 _ 704 702 1
705 704 904 9 15 65 48
_ _
7 825 _ 180 250 120 _ 466 80
773 760 1 763 763 895 8 13 _ 62 63
7 850 _ 180 250 30 466 50 ._ _._ 940 1031
1074 4 6 - ____ 58
-
7 850 _ 180 1 250 30 466 _ 50 0,1
951 1040 1076 3 5 ____ - 58
-
7 850 180 250 30 466 100 , 926 1004
1053 4 6 - 64
7 850 180 250 _ 30 _ 466 _ 100 940 1032
1067 5 6 - 64 ____ I
_
7 r 850 - 180 250 30 466 120 948. 904
948 1016 , 5 8 - 58
_ _____________
. 7 850 _ 180 250 30 466 120 953. 913
953 1019 5 6 ____ - 58
_
_
7 850 180 250 60 466 40 979 948 0 970
951 979 _ 1 8 67 64
- _
-
_ _
_ . . , .
7 850 180 250 _ 120 466 80 1032
988 0 984 992 1032 I 9 65 58
- .. ¨
7 850 180 SKIP SKIP 466 50 675
697 927 7 12 - - 55 Compara _
- - -
7 i 850 - 180 SKIP SKIP _
J 466 50 , . 666
691 911 7 12 55 Compara
0
Table 11 Mechanical properties for alloy no. 8 of Table 3.
K.)
to
.....1
K.)
'F.
.....1
0 EU
Hole
n.)
Hardn
o L
All Tempera Time at Tempera Time at
Tempera Time at UY LYS YP 02% Uniform
UTS(M
TotalElong ess EX.PanS
CO oy ture 1 Tempera ture 2 Tempera
ture 3 Tempera SCM (MP E Stre OYS(M pa) Elongatio ation
(vo orRA ton Note
1 No. ( C) ture i(s) ( C) lure 2 (s) ( C)
ture 3 (s) Pa) a) (%) Ss Pa) n(%) Ratio
to
i 0.5
_
_
co 8 800 180 250 30 466 50 731 750
978 8 12 - 35
_
8 800 180 250 30 466 50 753 783 982 6
11 - 35
_
_
_ 8 800 180 250 30 466 100 739 762 970
6 9 - 42
-
8 800 180 250 30 466 100 733 754 966
5 5 - 42 ,
_
_ 8 800 180 250 30 466 120 _ 557 _ 554
970 8 10 37
_
_
8 800 180 250 30 466 120 549 546
960 , 8 10 . 37 _
8 800 180 250 60 466 40 766 764 1 767 773 960
8 12 64 39
8 800 180 250 120 466 80 867 852 1 863 856 987
8 13 66 34
_
-
_
_ 8 8 800 180 SKIP SKIP 466 50 - _ 945 1008
1069 5 8 - 28 Compare
_ _
.
_
800 180 SKIP SKIP 466 50 _ 579 601 994
8 12 - 28 Compare
NJ
cr) 8 825 180 250 60 466 40 860 849 1 852 855 975 8
12 66 52 _
_
_
8 825 180 250 120 466 80 875 854 1
872 852 931 7 11 63 62 _
8 850 180 250 30 466 50 999.9 930 1007
1048 3 5 - 58 _
_ _ _ _ 8 850 180 250 30 466 50
948 - 1024 1071 3 6 - 58 _
_
8 850 180 250 30 466 100 937 1006
1063 3 6 - 49
8 850 180 250 30 466 . 100 _ 889 932 1005
5 _ 8 - 49
_ _
8 850 180 250 30 466 120 579 610 1003 7
11 69
_ _ 8 850 180 250 30 466 120 , 897 _ _ 965
1034 4 6 - 69 _
_
_
8 850 ., 180 250 60 466 40 1090 . 103 0 .
1048 1090 1 7 66 66
8 850 180 250 120 466 , 80 1068 _ 102 0
_ 1029 1068 1 _ 9 64 89 _
_
_
8 850 180 SKIP SKIP 466 50 648
692 931 _ 7 11 - 55 Compare
_ _
8 850 180 SKIP SKIP 466 50 667 688 939
7 11 - 55 Compare
,
0
Table 12 Mechanical properties for alloy no. 9 of Table 3.
K.)
to
-.I
IQ
IA
-...1
0
EU
Hole
1µ.) LY YP L
Hardn
02% Uniform Evans
0 All Tempera Time at Tempera Time at Tempera Time at UY
S E stre
UTS(M TotalElong ess
I-. oy ture 1 Tempera ture 2 Tempera
ture 3 Tempera S(M (he ,.% ss OYS(M 1.,a)
Elongatio ion Note
ation (%)
(MIA Ratio
co
I No. ( C) turn 1 (s) ( C) ture 2 (s) ( C)
tore 3 (a) Pa) ' a) µõ, Pa) n(%)
)
0 1 @
(Vo)
to
i 0.5
.,
Iv
9 - -
co 9 800 180 250 30 466 50 867
913 1040 6
9 800 180 250 39 466 50 870 937 1042
6 9 - -
9 800 180 250 30 466 . 1(X) _ 800 835 1001 7
10 -
_
9 800 180 250 30 466 100 800 846 997
7 11 - -
9 800 180 250 30 466 120 847 884 1015
6 9 - -
9 800 180 250 30 466 120 879 911 1015
6 10
9 BOO 180 250 60 466 40 890 923 998
6 9 65 58
9 800 180 250 120 466 80 816 839 969
7 11 64 63
_ ,
9 800 180 SKIP SKIP 466 50 _ 543 543 958
9 15 - - Compara
_ _
9 825 ¨ 180 250 60 466 40 968 998 1046
5 8 69 71
iv
--4 9 _ 825 180 , 250 120 466 80 1008 0
985 1003 1028 5 9 67 53
_ _
9 850 180 250 30 466 50 870 932 1043
6 8 - -
9 850 180 250 30 466 50 863 913 1038
6 9 -
9 850 180 250 30 466 100 894 936 1042
5 8 - -
,
9 850 180 250 30 466 100 _ 882 923 1039
6 10 -
_
9 850 _ 180 . 250 30 466 120 _ _ _
758 817 1121 6 10 - -
9 , 850 180 . 250 30 466 120 844 887 1011
6 10 - _
9 850 180 250 30 466 120 537 542 955
9 14 - -
9 850 180 . 250 60 466 40 ¨ 989 1006
, 1045 5 9 64 54
9 850 180 250 120 466 80 1000 998 0
990 998 1040 5 9 64 71
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Table 14 Mechanical properlies for alloy no. 11 of Table 3.
IV
tO
-4
N
ds=
--.1
0 EU
HOie
N L
Hardn
Uniform
Expans
iD All Tempera Time at Tempera Time at Tempera Time at LTY
LYS YP 0.2%
UTS(M TotalElong ess
i--, oy tare 1 Tempera lure 2 Tempera
hire 3 Tempera S(M (MP E Stre OYS(M Elangatio
ion Note
eo
Pa) ation (%) (BRA .
i No. ( C) ture 1 (s) ( C) ture 2 (a) ( C)
ture 3 (s) Pa) a) (%) as Pa) n(%) Ram
0
to 0.5
N 11 800 180 250 30 466 _
50 .
692 706
1047 _ 8 12 - 26
11 800 180 250 30 466 50 667 676
1037 9 12 - - 26
_
11 800 180 _ 250 30 466 100
719 751 1027 7 9 - 31
11 800 180 250 30 466 ¨ 100 _ 714 738
1021 7 7 - 31
11 800 180 . 250 30 466 _ 120
608 611 1041 9 12 28
- -
11 800 180 250 30 466 120 621 623
1056 10 14 - 28
11 800 180 250 60 466 - 40 727 731 1042
9 14 64 26
11 800 180 250 120 466 80 769 776
1085 9 13 68 28
- _ -
11 800 180 SKIP - SKIP 466 50 590
599 1070 9 12 - 26 Compara
_
_
_
11 800 180 SKIP SKIP 466 50 582
602 1060 9 12 - 26 Compara
NJ _ .
co 11 825 180 250 , 60 466 40
778 768 1 775 777 1029 9 13 63 36
_
_ _
11 825 180 , 250 120 466 80
820 807 1 820 809 995 9 15 61 36
_ 11 850 - 180 250 30 466 50 _- 940 1094
1132 6 8 _ 40
11 850 180 250 30 466 50 958 1112
1141 3 9 - 40
. _
11 850 180 250 30 466 100 893 1048
1105 6 8 - 44
11 850 180 _ 250 30 466 100 , - 907
1071 1127 _ 5 9 - 44
_
_
11 850 _ 180 , 250 30 _ 466 120 _
907 1037 1114 6 9 - 45
_
11 850 180 _ 250 30 466 120
894 1011 1107 6 9 - 45 _
- . .
11 850 180 _ 250 60 466 -
40 1100 1162 1 5 _ 67 42 .
11 850 - 180 250 _ 120 - 466
80 1072 1130 1 5 67 81
- ¨ - _
11 850 180 SKIP SKIP 466 50 668
720 1047 7 10 - 35 Compara
_
_
11 850 180 SKIP SKIP 466 50 - 675
712 1046 7 11 - 35 Compara
C)
Table 15 Mechanical properties for alloy no. 12 of Table 3.
K)
to
-4
Iµ)
il=
--.1
0 EU
Hole
ts.)
Hanln
o All Tempera
Time at Tempera Time at Tempera Time at UY L SY YEP _ 1 - 02% Uniform
Expans
1-`
CO oy ture 1 Tempera ture 2 Tempera
ture 3 Tempera S(M f.mp try. tre OYS(M UTPSar Elongatio
Totaffilong ess
ion Note
i No. CC) hire I (s) (CC) ture 2 (s) ( C)
ture 3 (s) Pa) ' a) `, ss Pa) n(%) ation (%) (HKA
Ratio
o
" )
to
CYO
I 0.5
tv _ _ . _
_
co 12 800 180 250 30 466 50 650 687
1194 7 10 - 21
12 800 180 250 30 466 50 660 698
1188 7 9 21
12 800 180 250 30 466 100 770 815
113 6 s 11 - 23
12 800 180 250 30 466 100 897 924
1138 8 10 - 23
_ 12 800 180 250 30 466 120 641 693
1171 8 11 - 23
_
12 800 ¨ _
180 250 30 466 120 656 710
1176 6 9 . 23
12 800 180 250 60 466 _ 40
_ 811 819 1169 8 12 67 26
12 800 ¨ 180 250 120 466 80 . 760 766
1168 8 12 67 25
12 800 180 SKIP SKIP 466 50 _ 661
720 1205 7 10 - 20 Compara
_
12 800 180 SKIP SKIP 466 _ _ 50
676 738 1225 7 10 - 20 Compara
12 825 180 250 60 466 40 849 846 I 852 856 1153
8 13 66 50
12 825 180 250 120 466 80 _ _ 1080
2 1038 1133 7 12 67 41
_ _
12 850 180 250 30 466 50 913 1072
1196 7 10 - 30
12 850 180 250 30 466 50 934 1102
1199 6 10 30
-
12 850 180 250 30 466 100 912
1080 1192 7 9 32
12 850 180 250 30 466 100 _ 943 1109
1199 7 9 - 32
_
12 850 180 250 30 466 _ - 120
837 954 118 6 7 10 - 34
12 850 180 250 30 466 _ 120 829
956 1181 7 9 - 34
-
12 850 180 250 60 466 _ 40 1177 3
1141 1178 7 11 68 , 49
-
12 850 180 250 120 466 80 1133 2
1 098 1152 7 10 66 60
-
12 850 180 SKIP SKIP 466 50 727
831 1 206 6 10 - 35 Compara
12 850 180 SKIP SKIP 466 50 736
868 1 230 6 10 - 35 Compara
CA 02972470 2017-06-27
WO 2016/115303
PCT/US2016/013338
[0042] It will be understood various modifications may be made to this
invention without
departing from the spirit and scope of it. Therefore, the limits of this
invention
should be determined from the appended claims.
31
