[0001]The present invention relates to a hot dip galvanized steel sheet and a method for producing
the same, mainly relates to a high strength hot dip galvanized steel sheet to be worked into
10 various shapes by press forming etc., as a steel sheet for automobile use and a method for
producing the same.
BACKGROUND
[0002]
15 In recent years, improvement of the fuel efficiency of automobiles has been sought from the
viewpoint of control of hot house gas emissions accompanying the campaign against global
warming. Application of high strength steel sheet for lightening the weight of car bodies and
securing collision safety has been increasingly expanding. In particular, recently, the need for
ultrahigh strength steel sheet with a tensile strength of 980 MPa or more has been increasingly
20 rising. Further, high strength hot dip galvanized steel sheet which is hot dip galvanized on its
surface is being sought for portions in car bodies where rust prevention is demanded.
[0003]
Hot dip galvanized steel sheet used for auto parts requires not only strength, but also press
formability, weldability, and various other types of workability necessary for forming parts.
25 Specifically, from the viewpoint of press formability, excellent elongation (total elongation in
tensile test: El) and stretch flangeability (hole expansion rate: ) are required from steel sheet.
Furthermore, if considering application of high strength steel sheet to automobiles used in cold
regions, it is required that the high strength steel sheet not fracture brittlely in a low temperature
environment, i.e., that it has an excellent low temperature toughness.
30 [0004]
In general, press formability deteriorates along with the higher strength of steel sheet. As
means for achieving both higher strength and press formability of steel, TRIP (transformation
induced plasticity) steel sheet utilizing transformation induced plasticity of retained austenite is
known.
35 [0005]
PTLs 1 to 3 disclose art relating to high strength TRIP steel sheet controlled in fractions of
2
structural constituents to predetermined ranges and improved in elongation and hole expansion
rates. Further, PTL 4 describes high strength steel sheet having a predetermined chemical
composition, and including, in terms of volume fraction, 15% or less of ferrite having an average
crystal grain diameter of 2 m or less, 2 to 15% of retained austenite having an average crystal
5 grain diameter of 2 m or less, 10% or less of martensite having an average crystal grain
diameter of 3 m or less, and a balance of bainite and tempered martensite having an average
crystal grain diameter of 6 m or less, wherein the average number of cementite grains having a
grain diameter of 0.04 m or more existing in the bainite and tempered martensite grains is 10 or
more, and describes that this high strength steel sheet has a tensile strength of 1180 MPa or more
10 and has a high elongation and hole expandability and excellent bending workability
accompanying the same.
[0006]
Furthermore, TRIP type high strength hot dip galvanized steel sheet is disclosed in several
literature.
15 [0007]
Normally, to produce hot dip galvanized steel sheet in a continuous annealing furnace, it is
necessary to heat the steel sheet to the reverse transformation temperature region (>Ac1) and
soak it, then in the middle of the process for cooling down to room temperature, dip it in a 460C
or so hot dip galvanizing bath. Alternatively, after heating and soaking, then cooling down to
20 room temperature, it is necessary to again heat the steel sheet to the hot dip galvanizing bath
temperature and dip it in the bath. Furthermore, usually, to produce hot dip galvannealed steel
sheet, it is necessary to perform alloying treatment after dipping the steel sheet in the coating
bath, then reheat the steel sheet to a 460C or more temperature region. For example, PTL 5
describes that the steel sheet is heated to Ac1 or more, is then rapidly cooled down to the
25 martensite transformation start temperature (Ms) or less, is then reheated to the bainite
transformation temperature region and held at the temperature region to stabilize the austenite
(austemper it), and is then reheated to the coating bath temperature or alloying treatment
temperature for galvannealing. However, with such a production method, since the martensite
and bainite is excessively tempered in the coating and alloying step, there was the problem that
30 the material quality became poor.
[0008]
PTLs 6 to 10 disclose a method for producing hot dip galvanized steel sheet comprising
cooling the steel sheet after coating and alloying treatment, then reheating it to temper the
martensite.
35
[CITATIONS LIST]
3
[PATENT LITERATURE]
[0009]
[PTL 1] WO 2013/051238
[PTL 2] Japanese Unexamined Patent Publication No. 2006-104532
5 [PTL 3] Japanese Unexamined Patent Publication No. 2011-184757
[PTL 4] WO 2017/179372
[PTL 5] WO 2014/020640
[PTL 6] Japanese Unexamined Patent Publication No. 2013-144830
[PTL 7] WO 2016/113789
10 [PTL 8] WO 2016/113788
[PTL 9] WO 2016/171237
[PTL 10] Japanese Unexamined Patent Publication No. 2017-48412
SUMMARY
15 [TECHNICAL PROBLEM]
[0010]
On the other hand, hot dip galvanized steel sheet used for automobiles used in cold regions
is required to not only possess press formability, but also not fracture in a brittle manner in a low
temperature environment. However, in the prior art, no sufficient study has necessarily been
20 made from the two viewpoints of the improvement of the press formability and the improvement
of such low temperature toughness. For this reason, there is still room for improvement of the
properties of hot dip galvanized steel sheet, in particular hot dip galvanized steel sheet used for
members for automobiles.
[0011]
25 Therefore, an object of the present invention is to provide hot dip galvanized steel sheet
excellent in press formability and low temperature toughness and having a tensile strength of
980 MPa or more and a method for producing the same.
[SOLUTION TO PROBLEM]
30 [0012]
The inventors engaged in intensive studies for solving this problem and as a result obtained
the following findings:
(i) In the continuous hot dip galvanization heat treatment step, martensite is formed by
cooling down to the Ms or less after coating or coating and alloying. Further, after that, the steel
35 may be reheated and held isothermally to suitably temper the martensite and, in the case of steel
sheet containing retained austenite, further stabilize the retained austenite. By such heat
4
treatment, the martensite is no longer excessively tempered by the coating or coating and
alloying, and therefore the balance of strength and ductility is improved.
(ii) Furthermore, the inventors discovered that if the Mn concentration at the interfaces of
different phases comprised of tempered martensite and soft structures contacting the same (i.e.,
5 ferrite and bainite) is a certain value or more, the low temperature toughness is improved. The
detailed mechanism is not clear, but in general it is believed that brittle fracture proceeds due to
the formation and propagation of cleavage cracks by dislocations piled up (gathered) at the
crystal grain boundaries and consequent concentration of stress at the grain boundaries. In
composite structure steel, it is believed that the regions where dislocations collect and stress
10 concentrates are the interfaces between different phases comprised of soft structures (ferrite and
bainite) and hard structures (tempered martensite). If the Mn concentration at the interfaces of
different phases is a certain value or more, it is believed that some sort of interaction occurs
between the group of dislocations and Mn atoms deposited at the interfaces of the different
phases and formation of cleavage cracks is suppressed. Further, the inventors discovered that the
15 above Mn concentration profile is realized by isothermal holding in the 480 to 600C or so
temperature region during a continuous hot dip galvanization heat treatment step. However, this
isothermal holding has to be performed before the austenite transforms to martensite. Further, if
performing this isothermal holding in this temperature region after coating, deterioration of the
powdering property of the coating layer etc., is caused. Therefore, the isothermal holding has to
20 be performed before the coating and alloying treatment.
(iii) Furthermore, the inventors discovered that the effect of the above (ii) becomes more
remarkable by limitation of the casting conditions at the time of continuous casting. That is, they
discovered that due to forming Mn segregated regions in advance at the time of casting, the Mn
concentration at the regions of interfaces of different phases explained in (ii) increased.
25 However, if making the Mn concentration excessively proceed, it was learned that the low
temperature toughness deteriorates. This is believed to be because if the Mn concentration
excessively proceeds, in the final structure, the Mn concentration increases not only at the
regions of interfaces of different phases, but also inside the grains of the tempered martensite. It
is believed that tempered martensite in which Mn is concentrated over the grain as a whole is
30 poor in toughness.
[0013]
The present invention was realized based on the above findings and specifically is as
follows:
(1) A hot dip galvanized steel sheet comprising a base steel sheet and a hot dip galvanized
35 layer on at least one surface of the base steel sheet, wherein the base steel sheet has a chemical
composition comprising, by mass%,
5
C: 0.050% to 0.350%,
Si: 0.10% to 2.50%,
Mn: 1.00% to 3.50%,
P: 0.050% or less,
5 S: 0.0100% or less,
Al: 0.001% to 1.500%,
N: 0.0100% or less,
O: 0.0100% or less,
Ti: 0% to 0.200%,
10 B: 0% to 0.0100%,
V: 0% to 1.00%,
Nb: 0% to 0.100%,
Cr: 0% to 2.00%,
Ni: 0% to 1.00%,
15 Cu: 0% to 1.00%,
Co: 0% to 1.00%,
Mo: 0% to 1.00%,
W: 0% to 1.00%,
Sn: 0% to 1.00%,
20 Sb: 0% to 1.00%,
Ca: 0% to 0.0100%,
Mg: 0% to 0.0100%,
Ce: 0% to 0.0100%,
Zr: 0% to 0.0100%,
25 La: 0% to 0.0100%,
Hf: 0% to 0.0100%,
Bi: 0% to 0.0100%,
REM other than Ce and La: 0% to 0.0100% and
a balance of Fe and impurities,
30 a steel microstructure at a range of 1/8 thickness to 3/8 thickness centered about a position
of 1/4 thickness from a surface of the base steel sheet contains, by volume fraction,
ferrite: 0% to 50%,
retained austenite: 0% to 30%,
tempered martensite: 5% or more,
35 fresh martensite: 0% to 10%, and
pearlite and cementite in total: 0% to 5%,
6
when there are remaining structures, the remaining structures consist of bainite, and
a number ratio of tempered martensite with a Mn concentration profile satisfying the
following formulas (1) and (2) is 0.2 or more with respect to the total number of the tempered
martensite:
5 [Mn]b /[Mn]a >1.2  (1)
[Mn]a /[Mn]<2.0  (2)
where [Mn] is the Mn content (mass%) in the base steel sheet, [Mn]a is the average Mn
concentration (mass%) in the tempered martensite, and [Mn]b is the Mn concentration (mass%)
at the interfaces of different phases of the tempered martensite and ferrite phase and bainite
10 phase.
(2) The hot dip galvanized steel sheet according to (1), wherein the steel microstructure
further contains, by volume fraction, retained austenite: 6% to 30%.
(3) A method for producing the hot dip galvanized steel sheet according to the above (1) or
(2), comprising a continuous casting step for continuously casting a slab having the chemical
15 composition according to the above (1), a hot rolling step for hot rolling the cast slab, and a hot
dip galvanizing step for hot dip galvanizing the obtained steel sheet, wherein
(A) the continuous casting step satisfies the conditions of the following (A1) and (A2):
(A1) a slab surface temperature at the time of the end of a secondary cooling is 500 to
1100C and
20 (A2) a casting rate is 0.4 to 3.0 m/s, and
(B) the hot dip galvanizing step comprises heating the steel sheet to first soak it, first
cooling then second soaking the first soaked steel sheet, dipping the second soaked steel sheet in
a hot dip galvanizing bath, second cooling the coated steel sheet, and heating the second cooled
steel sheet then third soaking it, and further satisfies the conditions of the following (B1) to (B6):
25 (B1) in the heating of the steel sheet before the first soaking, the average heating rate
from 650C to a maximum heating temperature of Ac1+30C or more and 950C or less is
0.5C/s to 10.0C/s,
(B2) the steel sheet is held at the maximum heating temperature for 1 second to 1000
seconds (first soaking),
30 (B3) an average cooling rate in a temperature range of 700 to 600C at the first cooling
is 10 to 100C/s,
(B4) the first cooled steel sheet is held in a range of 480 to 600C for 80 seconds to 500
seconds (second soaking),
(B5) the second cooling is performed down to Ms-50C or less, and
35 (B6) the second cooled steel sheet is heated to a temperature region of 200 to 420C,
then held in the temperature region for 5 to 500 seconds (third soaking).
7
[ADVANTAGEOUS EFFECTS OF INVENTION]
[0014]
According to the present invention, it is possible to obtain hot dip galvanized steel sheet
5 excellent in press formability, specifically ductility and hole expandability and further low
temperature toughness.
BRIEF DESCRIPTION OF DRAWINGS
[0015]
10 FIG. 1 shows a reference view of an SEM secondary electron image.
FIG. 2 is a temperature-thermal expansion curve when simulating a heat cycle
corresponding to hot dip galvanization treatment according to the embodiment of the present
invention by a thermal expansion measurement apparatus.
15 DESCRIPTION OF EMBODIMENTS
[0016]

The hot dip galvanized steel sheet according to the embodiment of the present invention
comprises a base steel sheet and a hot dip galvanized layer on at least one surface of the base
20 steel sheet, wherein the base steel sheet has a chemical composition comprising, by mass%,
C: 0.050% to 0.350%,
Si: 0.10% to 2.50%,
Mn: 1.00% to 3.50%,
P: 0.050% or less,
25 S: 0.0100% or less,
Al: 0.001% to 1.500%,
N: 0.0100% or less,
O: 0.0100% or less,
Ti: 0% to 0.200%,
30 B: 0% to 0.0100%,
V: 0% to 1.00%,
Nb: 0% to 0.100%,
Cr: 0% to 2.00%,
Ni: 0% to 1.00%,
35 Cu: 0% to 1.00%,
Co: 0% to 1.00%,
8
Mo: 0% to 1.00%,
W: 0% to 1.00%,
Sn: 0% to 1.00%,
Sb: 0% to 1.00%,
5 Ca: 0% to 0.0100%,
Mg: 0% to 0.0100%,
Ce: 0% to 0.0100%,
Zr: 0% to 0.0100%,
La: 0% to 0.0100%,
10 Hf: 0% to 0.0100%,
Bi: 0% to 0.0100%,
REM other than Ce and La: 0% to 0.0100% and
a balance of Fe and impurities,
a steel microstructure at a range of 1/8 thickness to 3/8 thickness centered about a position
15 of 1/4 thickness from a surface of the base steel sheet contains, by volume fraction,
ferrite: 0% to 50%,
retained austenite: 0% to 30%,
tempered martensite: 5% or more,
fresh martensite: 0% to 10%, and
20 pearlite and cementite in total: 0% to 5%,
when there are remaining structures, the remaining structures consist of bainite, and
a number ratio of tempered martensite with a Mn concentration profile satisfying the
following formulas (1) and (2) is 0.2 or more with respect to the total number of the tempered
martensite:
25 [Mn]b /[Mn]a >1.2  (1)
[Mn]a /[Mn]<2.0  (2)
where [Mn] is the Mn content (mass%) in the base steel sheet, [Mn]a is the average Mn
concentration (mass%) in the tempered martensite, and [Mn]b is the Mn concentration (mass%)
at the interfaces of different phases of the tempered martensite and ferrite phase and bainite
30 phase.
[0017]
[Chemical Composition]
First, the reasons for limitation of the chemical composition of the base steel sheet
according to the embodiment of the present invention (below, also simply referred to as the
35 “steel sheet”) as described above will be explained. In this Description, the “%” used in
prescribing the chemical composition are all “mass%” unless otherwise indicated. Further, in
9
this Description, “to” when showing the ranges of numerical values unless otherwise indicated
will be used in the sense including the lower limit values and upper limit values of the numerical
values described before and after it.
[0018]
5 [C: 0.050% to 0.350%]
C is an element essential for securing the steel sheet strength. If less than 0.050%, the
required high strength cannot be obtained, and therefore the content of C is 0.050% or more. The
content of C may be 0.070% or more, 0.080% or more, 0.100% or more as well. On the other
hand, if more than 0.350%, the workability or weldability falls, and therefore the content of C is
10 0.350% or less. The content of C may be 0.340% or less, 0.320% or less, or 0.300% or less as
well.
[0019]
[Si: 0.10% to 2.50%]
Si is an element suppressing formation of iron carbides and contributing to improvement of
15 strength and shapeability, but excessive addition causes the weldability of the steel sheet to
deteriorate. Therefore, the content is 0.10 to 2.50%. The content of Si may be 0.20% or more,
0.30% or more, 0.40% or more, or 0.50% or more as well and/or may be 2.20% or less, 2.00% or
less, or 1.90% or less as well.
[0020]
20 [Mn: 1.00% to 3.50%]
Mn (manganese) is a powerful austenite stabilizing element and an element effective for
increasing the strength of the steel sheet. Excessive addition causes the weldability or low
temperature toughness to deteriorate. Therefore, the content is 1.00 to 3.50%. The content of Mn
may be 1.10% or more, 1.30% or more, or 1.50% or more as well and/or may be 3.30% or less,
25 3.10% or less, or 3.00% or less as well.
[0021]
[P: 0.050% or less]
P (phosphorus) is a solution strengthening element and an element effective for increasing
the strength of the steel sheet. Excessive addition causes the weldability and toughness to
30 deteriorate. Therefore, the content of P is limited to 0.050% or less. Preferably it is 0.045% or
less, 0.035% or less, or 0.020% or less. However, since extreme reduction of the content of P
would result in high dephosphorizing costs, from the viewpoint of economics, a lower limit of
0.001% is preferable.
[0022]
35 [S: 0.0100% or less]
S (sulfur) is an element contained as an impurity and forms MnS in steel to cause the
10
toughness and hole expandability to deteriorate. Therefore, the content of S is restricted to
0.0100% or less as a range where the toughness and hole expandability do not remarkably
deteriorate. Preferably it is 0.0050% or less, 0.0040% or less, or 0.0030% or less. However,
since extreme reduction of the content of S would result in high desulfurizing costs, from the
5 viewpoint of economics, a lower limit of 0.0001% is preferable.
[0023]
[Al: 0.001% to 1.500%]
Al (aluminum) is added in at least 0.001% for deoxidation of the steel. However, even if
excessively adding it, not only does the effect become saturated and is a rise in cost invited, but
10 also the transformation temperature of the steel is raised and the load at the time of hot rolling is
increased. Therefore, an amount of Al of 1.500% is the upper limit. Preferably it is 1.200% or
less, 1.000% or less, or 0.800% or less.
[0024]
[N: 0.0100% or less]
15 N (nitrogen) is an element contained as an impurity. If its content is more than 0.0100%, it
forms coarse nitrides in the steel and causes deterioration of the bendability and hole
expandability. Therefore, the content of N is limited to 0.0100% or less. Preferably it is 0.0080%
or less, 0.0060% or less, or 0.0050% or less. However, since extreme reduction of the content of
N would result in high denitriding costs, from the viewpoint of economics, a lower limit of
20 0.0001% is preferable.
[0025]
[O: 0.0100% or less]
O (oxygen) is an element contained as an impurity. If its content is more than 0.0100%, it
forms coarse oxides in the steel and causes deterioration of the bendability and hole
25 expandability. Therefore, the content of O is limited to 0.0100% or less. Preferably it is 0.0080%
or less, 0.0060% or less, or 0.0050% or less. However, from the viewpoint of the producing
costs, a lower limit of 0.0001% is preferable.
[0026]
The basic chemical composition of the base steel sheet according to the embodiment of the
30 present invention is as explained above. The base steel sheet may however further contain the
following elements according to need.
[0027]
[Ti: 0% to 0.200%, V: 0% to 1.00%, Nb: 0% to 0.100%, Cr: 0% to 2.00%, Ni: 0% to 1.00%, Cu:
0% to 1.00%, Co: 0% to 1.00%, Mo: 0% to 1.00%, B: 0% to 0.0100%, W: 0% to 1.00%, Sn: 0%
35 to 1.00%, and Sb: 0% to 1.00%]
Ti (titanium), V (vanadium), Nb (niobium), Cr (chromium), Ni (nickel), Cu (copper), Co
11
(cobalt), Mo (molybdenum), B (boron), W (tungsten), Sn (tin), and Sb (antimony) are all
elements effective for raising the strength of steel sheet. For this reason, one or more of these
elements may be added in accordance with need. However, if excessively adding these elements,
the effect becomes saturated and in particular an increase in cost is invited. Therefore, the
5 contents are Ti: 0% to 0.200%, V: 0% to 1.00%, Nb: 0% to 0.100%, Cr: 0% to 2.00%, Ni: 0% to
1.00%, Cu: 0% to 1.00%, Co: 0% to 1.00%, Mo: 0% to 1.00%, B: 0% to 0.0100%, W: 0% to
1.00%, Sn: 0% to 1.00%, Sb: 0% to 1.00%. The elements may also be 0.005% or more or
0.010% or more. In particular, the content of B may be 0.0001% or more or 0.0005% or more.
[0028]
10 [Ca: 0% to 0.0100%, Mg: 0% to 0.0100%, Ce: 0% to 0.0100%, Zr: 0% to 0.0100%, La: 0% to
0.0100%, Hf: 0% to 0.0100%, Bi: 0% to 0.0100%, and REM other than Ce and La: 0% to
0.0100%]
Ca (calcium), Mg (magnesium), Ce (cerium), Zr (zirconium), La (lanthanum), Hf
(hafnium), and REM (rare earth elements) other than Ce and La are elements contributing to
15 microdispersion of inclusions in the steel. Bi (bismuth) is an element lightening the
microsegregation of Mn, Si, and other substitution type alloying elements in the steel. Since
these respectively contribute to improvement of the workability of steel sheet, one or more of
these elements may be added in accordance with need. However, excessive addition causes
deterioration of the ductility. Therefore, a content of 0.0100% is the upper limit. Further, the
20 elements may be 0.0005% or more or 0.0010% or more as well.
[0029]
In the base steel sheet according to the embodiment of the present invention, the balance
other than the above elements is comprised of Fe and impurities. “Impurities” are constituents
entering due to various factors in the producing process, first and foremost the raw materials
25 such as the ore and scrap, when industrially producing the base steel sheet and encompass all
constituents not intentionally added to the base steel sheet according to the embodiment of the
present invention. Further, “impurities” encompass all elements other than the constituents
explained above contained in the base steel sheet in levels where the actions and effects
distinctive to those elements do not affect the properties of the hot dip galvanized steel sheet
30 according to the embodiment of the present invention.
[0030]
[Steel Structures Inside Steel Sheet]
Next, the reasons for limitation of the internal structure of the base steel sheet according to
the embodiment of the present invention will be explained.
35 [0031]
[Ferrite: 0 to 50%]
12
Ferrite is a soft structure excellent in ductility. It may be included to improve the elongation
of steel sheet in accordance with the demanded strength or ductility. However, if excessively
contained, it becomes difficult to secure the desired steel sheet strength. Therefore, the content is
a volume fraction of 50% as the upper limit and may be 45% or less, 40% or less, or 35% or less.
5 The content of ferrite may be a volume fraction of 0%. For example, it may be 3% or more, 5%
or more, or 10% or more.
[0032]
[Tempered martensite: 5% or more]
Tempered martensite is a high strength tough structure and is an essential metallic structure
10 in the present invention. To balance the strength, ductility, and hole expandability at a high level,
it is included in a volume fraction of at least 5% or more. Preferably, it is a volume fraction of
10% or more. It may be 15% or more or 20% or more as well. For example, the content of the
tempered martensite may be a volume fraction of 90% or less, 85% or less, 80% or less, or 70%
or less.
15 [0033]
[Fresh martensite: 0 to 10%]
In the present invention, fresh martensite means martensite which is not tempered, i.e.,
martensite not containing carbides. This fresh martensite is a brittle structure, so becomes a
starting point of fracture at the time of plastic deformation and causes deterioration of the local
20 ductility of the steel sheet. Therefore, the content is a volume fraction of 0 to 10%. More
preferably it is 0 to 8% or 0 to 5%. The content of fresh martensite may be a volume fraction of
1% or more or 2% or more.
[0034]
[Retained austenite: 0% to 30%]
25 Retained austenite improves the ductility of steel sheet due to the TRIP effect of
transformation into martensite due to work induced transformation during deformation of steel
sheet. On the other hand, to obtain a large amount of retained austenite, C and other alloying
elements must be included in large amounts. For this reason, the upper limit value of the retained
austenite is a volume fraction of 30%. It may be 25% or less or 20% or less as well. However, if
30 desiring to improve the ductility of the steel sheet, the content is preferably a volume fraction of
6% or more, 8% or more, or 10% or more. Further, if the content of the retained austenite is 6%
or more, the content of Si in the base steel sheet is preferably, by mass%, 0.50% or more.
[0035]
[Pearlite and cementite in total: 0 to 5%]
35 Pearlite includes hard coarse cementite and forms a starting point of fracture at the time of
plastic deformation, so causes the local ductility of the steel sheet to deteriorate. Therefore, the
13
content, together with the cementite, is a volume fraction of 0 to 5%. It may also be 0 to 3% or 0
to 2%.
[0036]
The remaining structures besides the above structures may be 0%, but if there are any
5 present, they are bainite. The remaining bainite structures may be upper bainite or lower bainite
or may be mixed structures of the same.
[0037]
[Number ratio of tempered martensite with Mn concentration profile satisfying formulas (1) and
(2) of 0.2 or more with respect to total number of tempered martensite]
10 [Mn]b /[Mn]a >1.2  (1)
[Mn]a /[Mn]<2.0  (2)
where [Mn] is the Mn content (mass%) in the base steel sheet, [Mn]a is the average Mn
concentration (mass%) in the tempered martensite, and [Mn]b is the Mn concentration (mass%)
at the interfaces of different phases of the tempered martensite and ferrite phase and bainite
15 phase.
[0038]
In the present invention, the above conditions have to be satisfied to obtain the desired low
temperature toughness. To obtain the effect of raising the toughness by strengthening the
interfaces of the different phases, [Mn]b /[Mn]a must be over 1.2. On the other hand, if
20 [Mn]a /[Mn] becomes 2.0 or more, the toughness of the tempered martensite itself deteriorates. If
the number ratio of the tempered martensite simultaneously satisfying the above conditions
becomes 0.2 or more with respect to the total number of tempered martensite, the low
temperature toughness rises to the desired level. The number ratio of the tempered martensite
may be 0.3 or more or 0.4 or more and/or may be 1.0 or less or 0.9 or less.
25 [0039]
The fractions of the steel structures of the hot dip galvanized steel sheet are evaluated by the
SEM-EBSD method (electron backscatter diffraction method) and SEM secondary electron
image observation.
[0040]
30 First, a sample is taken from the cross-section of thickness of the steel sheet parallel to the
rolling direction so that the cross-section of thickness at the center position in the width direction
becomes the observed surface. The observed surface is machine polished and finished to a
mirror surface, then electrolytically polished. Next, in one or more observation fields at a range
of 1/8 thickness to 3/8 thickness centered about 1/4 thickness from the surface of the base steel
sheet at the observed surface, a total area of 2.010- 9 m
2
35 or more is analyzed for crystal
structures and orientations by the SEM-EBSD method. The data obtained by the EBSD method
14
is analyzed using “OIM Analysis 6.0” made by TSL. Further, the distance between evaluation
points (steps) is 0.03 to 0.20 m. Regions judged to be FCC iron from the results of observation
are deemed retained austenite. Further, boundaries with differences in crystal orientation of 15
degrees or more are deemed grain boundaries to obtain a crystal grain boundary map.
5 [0041]
Next, the same sample as that observed by EBSD is corroded by Nital and observed by
secondary electron image for the same fields as observation by EBSD. Since observing the same
fields as the time of EBSD measurement, Vickers indents and other visual marks may be
provided in advance. From the obtained secondary electron image, the area ratios of the ferrite,
10 retained austenite, bainite, tempered martensite, fresh martensite, and pearlite are respectively
measured and the results deemed the volume fractions. Regions having lower structures in the
grains and having several variants of cementite, more specifically two or more variants,
precipitating are judged to be tempered martensite (for example, see reference drawing of FIG.
1). Regions where cementite precipitates in lamellar form are judged to be pearlite (or pearlite
15 and cementite in total). Regions which are small in brightness and in which no lower structures
are observed are judged to be ferrite (for example, see reference drawing of FIG. 1). Regions
which are large in brightness and in which lower structures are not revealed by etching are
judged to be fresh martensite and retained austenite (for example, see reference drawing of FIG.
1). Regions not corresponding to any of the above regions are judged to be bainite. The volume
20 ratios of the same are calculated by the point counting method and used as the volume ratios of
the structures. The volume ratio of the fresh martensite can be found by subtracting the volume
ratio of retained austenite found by X-ray diffraction.
[0042]
The volume ratio of retained austenite is measured by the X-ray diffraction method. At a
25 range of 1/8 thickness to 3/8 thickness centered about 1/4 thickness from the surface of the base
steel sheet, a surface parallel to the sheet surface is polished to a mirror finish and measured for
area ratio of FCC iron by the X-ray diffraction method. This is used as the volume fraction of the
retained austenite.
[0043]
30 In the present invention, the Mn concentration at the interfaces of the different phases of
tempered martensite and ferrite and bainite is found by the STEM-EELS method. Specifically,
for example, it is found by the method disclosed in METALLURGICAL AND MATERIALS
TRANSACTIONS A: vol. 45A, p.1877 to 1888. First, a sample is taken from the cross-section
of thickness of the steel sheet parallel to the rolling direction so that the cross-section of
35 thickness at the center position in the width direction becomes the observed surface. The
observed surface is machine polished and finished to a mirror surface, then electrolytically
15
polished. Next, in one or more observation fields at a range of 1/8 thickness to 3/8 thickness
centered about 1/4 thickness from the surface of the base steel sheet at the observed surface, a
total area of 2.010- 9 m
2
or more is analyzed for crystal structures and orientations by the SEMEBSD method to identify the tempered martensite and ferrite and bainite. Next, the region
5 including the interfaces of the different phases is extracted by FIB in the SEM. After that, Ar ion
milling etc., is used to reduce the thickness down to about 70 nm. The electron energy loss
spectrum (EELS) is obtained along a line traversing the interfaces of the different phases by
aberration spectrum STEM from the test piece reduced in thickness. The above measurement is
performed for the individual interfaces for at least five or more, preferably 10 or more samples
10 of the tempered martensite. The maximum value of the Mn concentration in the Mn
concentration profile measured traversing the interfaces of the different phases is [Mn]b . The
value obtained by averaging the Mn concentration profile at the tempered martensite side
leaving aside the regions of interfaces of different phases is [Mn]a . [Mn] is the same as the Mn
content in the steel composition. The scan steps at the time of line analysis is preferably 0.1 nm
15 or so. In the present invention, for example, if measuring 10 different tempered martensite, if the
number of tempered martensite satisfying the following formulas (1) and (2) is two or more, it is
judged if the number ratio of the tempered martensite where the Mn concentration profile
satisfying the formulas (1) and (2) is 0.2 or more with respect to the total number of tempered
martensite:
20 [Mn]b /[Mn]a >1.2  (1)
[Mn]a /[Mn]<2.0  (2)
[0044]
(Hot dip galvanized layer)
The base steel sheet according to the embodiment of the present invention has a hot dip
25 galvanized layer on at least one surface, preferably on both surfaces. This coating layer may be a
hot dip galvanized layer or hot dip galvannealed layer having any composition known to persons
skilled in the art and may include Al and other additive elements in addition to Zn. Further, the
amount of deposition of the coating layer is not particularly limited and may be a general amount
of deposition.
30 [0045]

Next, the method for producing the hot dip galvanized steel sheet according to the
embodiment of the present invention will be explained. The following explanation is meant to
illustrate the characteristic method for producing the hot dip galvanized steel sheet according to
35 the embodiment of the present invention and is not meant to limit the hot dip galvanized steel
sheet to one produced by the production method explained below.
16
[0046]
The method for producing the hot dip galvanized steel sheet comprises a continuous casting
step for continuously casting a slab having the same chemical composition as the chemical
composition explained above relating to the base steel sheet, a hot rolling step for hot rolling the
5 cast slab, and a hot dip galvanizing step for hot dip galvanizing the obtained steel sheet, wherein
(A) the continuous casting step satisfies the conditions of the following (A1) and (A2):
(A1) a slab surface temperature at the time of the end of a secondary cooling is 500 to
1100C and
(A2) a casting rate is 0.4 to 3.0 m/s, and
10 (B) the hot dip galvanizing step comprises heating the steel sheet to first soak it, first
cooling then second soaking the first soaked steel sheet, dipping the second soaked steel sheet in
a hot dip galvanizing bath, second cooling the coated steel sheet, and heating the second cooled
steel sheet then third soaking it, and further satisfies the conditions of the following (B1) to (B6):
(B1) in the heating of the steel sheet before the first soaking, the average heating rate
15 from 650C to a maximum heating temperature of Ac1+30C or more and 950C or less is
0.5C/s to 10.0C/s,
(B2) the steel sheet is held at the maximum heating temperature for 1 second to 1000
seconds (first soaking),
(B3) an average cooling rate in a temperature range of 700 to 600C at the first cooling
20 is 10 to 100C/s,
(B4) the first cooled steel sheet is held in a range of 480 to 600C for 80 seconds to 500
seconds (second soaking),
(B5) the second cooling is performed down to Ms-50C or less, and
(B6) the second cooled steel sheet is heated to a temperature region of 200 to 420C,
25 then held in the temperature region for 5 to 500 seconds (third soaking).
[0047]
Below, the method for producing the hot dip galvanized steel sheet will be explained in
detail.
[0048]
30 [(A) Continuous Casting Step]
[Slab surface temperature at time of end of secondary cooling: 500 to 1100C and casting rate:
0.4 to 3.0 m/min]
The steel slab used in the present invention is cast by the continuous casting method. The
thickness of the slab is generally 200 to 300 mm, for example, is 250 mm. If the slab surface
35 temperature at the time of end of the secondary cooling by water at the time of continuous
casting (time of end of cooling at secondary cooling zone at casting exit side) rises above
17
1100C or the casting rate falls below 0.4 m/min, the degree of segregation of Mn excessively
rises and [Mn]a /[Mn] tends to become 2.0 or more. On the other hand, if the slab surface
temperature falls below 500C or the casting speed rises above 3.0 m/min, the degree of Mn
segregation becomes insufficient, so [Mn]b /[Mn]a tends to become 1.2 or less. The slab surface
5 temperature at the time of end of the secondary cooling may be 600C or more or 700C or more
and/or may be 1050C or less. Further, the casting rate may be 0.6 m/min or more or 0.8 m/min
or more and/or may be 2.5 m/min or less or 2.0 m/min or less. The slab surface temperature is
measured by a radiation thermometer.
[0049]
10 [Hot Rolling Step]
In this method, the hot rolling step is not particularly limited and can be performed under
any suitable conditions. Therefore, the following explanation relating to the hot rolling step is
intended as a simple illustration and is not intended as limiting the hot rolling step in the present
method to one performed under the specific conditions as explained below.
15 [0050]
First, in the hot rolling step, a slab having the same chemical composition as the chemical
composition explained above relating to the base steel sheet is heated before hot rolling. The
heating temperature of the slab is not particularly limited, but for sufficient dissolution of the
borides, carbides, etc., generally 1150C or more is preferable.
20 [0051]
[Rough rolling]
In this method, for example, the heated slab may be rough rolled before the finish rolling so
as to adjust the sheet thickness etc. Such rough rolling is not particularly limited, it is preferable
to perform it to give a total rolling reduction at 1050C or more of 60% or more. If the total
25 rolling reduction is less than 60%, since the recrystallization during hot rolling becomes
insufficient, sometimes this leads to unevenness of the structure of the hot rolled sheet. The
above total rolling reduction may, for example, be 90% or less.
[0052]
[Finish rolling inlet side temperature: 900 to 1050C, finish rolling exit side temperature: 850C
30 to 1000C, and total rolling reduction: 70 to 95%]
The finish rolling is performed in a range satisfying the conditions of a finish rolling inlet
side temperature of 900 to 1050C, a finish rolling exit side temperature of 850C to 1000C,
and a total rolling reduction of 70 to 95%. If the finish rolling inlet side temperature falls below
900C, the finish rolling exit side temperature falls below 850C, or the total rolling reduction
35 exceeds 95%, the hot rolled steel sheet develops texture, so sometimes anisotropy appears in the
final finished product sheet. On the other hand, if the finish rolling inlet side temperature rises
18
above 1050C, the finish rolling exit side temperature rises above 1000C, or the total rolling
reduction falls below 70%, the hot rolled steel sheet becomes coarser in crystal grain size
sometimes leading to coarsening of the final finished product sheet structure and in turn
deterioration of the workability. For example, the finish rolling inlet side temperature may be
5 950C or more. The finish rolling exit side temperature may be 900C or more. The total rolling
reduction may be 75% or more or 80% or more.
[0053]
[Coiling temperature: 450 to 680C]
The coiling temperature is 450 to 680C. If the coiling temperature falls below 450C, the
10 strength of the hot rolled sheet becomes excessive and sometimes the cold rolling ductility is
impaired. On the other hand, if the coiling temperature exceeds 680C, the cementite coarsens
and undissolved cementite remains, so sometimes the workability is impaired. The coiling
temperature may be 470C or more and/or may be 650C or less.
[0054]
15 In the present method, the obtained hot rolled steel sheet (hot rolled coil) may be pickled or
otherwise treated as required. The hot rolled coil may be pickled by any ordinary method.
Further, the hot rolled coil may be skin pass rolled to correct its shape and improve its pickling
ability.
[0055]
20 [Cold Rolling Step]
In this method, after the hot rolling and/or pickling, the steel sheet may be heat treated as is
by a continuous hot dip galvanization line or may be cold rolled, then heat treated on a
continuous hot dip galvanization line. If performing cold rolling, the cold rolling reduction is
preferably 25% or more or 30% or more. On the other hand, since excessive rolling reduction
25 results in an excessive rolling force and leads to increases in load of the cold rolling mill, the
upper limit is preferably 75% or 70%.
[0056]
[(B) Hot Dip Galvanization Step]
[Average heating rate from 650C to maximum heating temperature of Ac1+30C or more and
30 950C or less: 0.5 to 10.0C/s]
In this method, after the hot rolling step, the obtained steel sheet is coated in a hot dip
galvanization step. In the hot dip galvanization step, first, the steel sheet is heated and subjected
to first soaking treatment. At the time of heating the steel sheet, the average heating rate from
650C to the maximum heating temperature of Ac1+30C or more and 950C or less is limited
35 to 0.5 to 10.0C/s. If the heating rate is more than 10.0C/s, the recrystallization of ferrite does
not sufficiently proceed and sometimes the elongation of the steel sheet becomes poor. On the
19
other hand, if the average heating rate falls below 0.5C/s, the austenite becomes coarse, so
sometimes the finally obtained steel structures become coarse. This average heating rate may be
1.0C/ or more and/or may be 8.0C/s or less or 5.0C/s or less. In the present invention, the
“average heating rate” means the value obtained by dividing the difference between 650C and
5 the maximum heating temperature by the elapsed time from 650C to the maximum heating
temperature.
[0057]
[First soaking treatment: Holding at maximum heating temperature of Ac1+30C or more and
950C or less for 1 second to 1000 seconds]
10 To cause sufficient austenite transformation to proceed, the steel sheet is heated to at least
Ac1+30C or more and held at that temperature (maximum heating temperature) as soaking
treatment. However, if excessively raising the heating temperature, not only is deterioration of
the toughness due to coarsening of the austenite grain size invited, but also damage to the
annealing facilities is led to. For this reason, the upper limit is 950C, preferably 900C. If the
15 soaking time is short, austenite transformation does not sufficiently proceed, so the time is at
least 1 second or more. Preferably it is 30 seconds or more or 60 seconds or more. On the other
hand, if the soaking time is too long, the productivity is damaged, so the upper limit is 1000
seconds, preferably 500 seconds. During soaking, the steel sheet does not necessarily have to be
held at a constant temperature. It may also fluctuate within a range satisfying the above
20 conditions. The “holding” in the first soaking treatment and the later explained second soaking
treatment and third soaking treatment means maintaining the temperature within a range of a
predetermined temperature20C, preferably 10C, in a range not exceeding the upper limit
value and lower limit value prescribed in the soaking treatments. Therefore, for example, a
heating or cooling operation which gradually heats or gradually cools whereby the temperature
25 fluctuates by more than 40C, preferably 20C, with the temperature ranges prescribed in the
soaking treatments are not included in the first, second, and third soaking treatments according
to the embodiment of the present invention.
[0058]
[First cooling: Average cooling rate in temperature range of 700 to 600C: 10 to 100C/s]
30 After holding at the maximum heating temperature, the steel sheet is cooled by the first
cooling. The cooling stop temperature is 480C to 600C of the following second soaking
temperature. The average cooling rate in a temperature range of 700C to 600C is 10 to
100C/s. If the average cooling rate is less than 10C/s, sometimes the desired ferrite fraction
cannot be obtained. The average cooling rate may be 15C/s or more or 20C/s or more. Further,
35 the average cooling rate may also be 80C/s or less or 60C/s or less. In the present invention,
“the average cooling rate” means the value obtained by dividing the temperature difference
20
between 700C and 600C, i.e., 100C, by the elapsed time from 700C to 600C.
[0059]
[Second soaking treatment: Holding in range of 480C to 600C for 80 to 500 seconds]
Second soaking treatment holding the steel sheet in range of 480C to 600C for 80 to 500
5 seconds is performed by making Mn segregate at the interfaces of the different phases comprised
of austenite and ferrite and bainite. The austenite at that time later becomes tempered martensite.
That is, due to the second soaking treatment, Mn segregates at the interfaces of the different
phases comprised of austenite and ferrite and bainite and due to the later second cooling and
third soaking treatment, the austenite is transformed to martensite and is tempered, whereby as a
10 result the Mn concentration at the interfaces of the different phases comprised of austenite and
ferrite and bainite increases. If the temperature of the second soaking treatment falls below
480C or becomes higher than 600 or if the holding time falls below 80 seconds, the
segregation of the Mn does not sufficiently proceed. On the other hand, if the holding time
becomes more than 500 seconds, since bainite transformation will excessively proceed, the metal
15 structures according to the embodiment of the present invention will not be able to be obtained.
The temperature of the second soaking treatment may be 500C or more and/or may be 570C or
less. Further, the holding time may be 95 seconds or more and/or may be 460 seconds or less. In
relation to this, even if simply suitably performing the second soaking treatment, if not suitably
forming the Mn segregated regions in the continuous casting step, the Mn concentration at the
20 interfaces of the different phases decreases. Therefore, in the method for producing the hot dip
galvanized steel sheet according to an embodiment of the present invention, to make the Mn
concentration at the interface of the different phases increase, it is important to satisfy the
conditions of (A1) and (A2) explained above in the continuous casting step while suitably
performing the second soaking treatment in the hot dip galvanization step.
25 In the present method, to produce the hot dip galvanized steel sheet according to an
embodiment of the present invention, after the second soaking treatment, predetermined coating
treatment has to be performed, but if the second soaking treatment were performed after dipping
in the coating bath, sometimes the powdering resistance of the coated layer would remarkably
deteriorate. This is because if performing heat treatment after dipping in a coating bath at 480C
30 or more for 80 seconds or more, the alloying reaction between the coating and steel sheet
excessively proceeds and the structure inside the coating film changes from the  phases
excellent in ductility to the Γ phases poor in ductility.
[0060]
After the second soaking treatment, the steel sheet is dipped in a hot dip galvanizing bath.
35 The steel sheet temperature at this time has little effect on the performance of the steel sheet, but
if the difference between the steel sheet temperature and the coating bath temperature is too
21
large, since the coating bath temperature will change and sometimes hinder operation, provision
of a step for cooling the steel sheet to a range of the coating bath temperature-20C to the
coating bath temperature+20C is desirable. The hot dip galvanization may be performed by an
ordinary method. For example, the coating bath temperature may be 440 to 460C and the
5 dipping time may be 5 seconds or less. The coating bath is preferably a coating bath containing
Al in 0.08 to 0.2%, but as impurities, Fe, Si, Mg, Mn, Cr, Ti, and Pb may also be contained.
Further, controlling the basis weight of the coating by gas wiping or another known method is
preferable. The basis weight is preferably 25 to 75 g/m2
per side.
[0061]
10 [Alloying treatment]
For example, the hot dip galvanized steel sheet formed with the hot dip galvanized layer
may be treated to alloy it as required. In this case, if the alloying treatment temperature is less
than 460C, not only does the alloying rate becomes slower and is the productivity hindered, but
also uneven alloying treatment occurs, so the alloying treatment temperature is 460C or more.
15 On the other hand, if the alloying treatment temperature is more than 600C, sometimes the
alloying excessively proceeds and the coating adhesion of the steel sheet deteriorates. Further,
sometimes pearlite transformation proceeds and the desired metallic structure cannot be
obtained. Therefore, the alloying treatment temperature is 600C or less.
[0062]
20 [Second cooling: Cooling to Ms-50C or less]
The steel sheet after the coating treatment or coating and alloying treatment is cooled by the
second cooling which cools it down to the martensite transformation start temperature (Ms)-
50C or less so as to make part or the majority of the austenite transform to martensite. The
martensite produced here is tempered by the subsequent reheating and third soaking treatment to
25 become tempered martensite. If the cooling stop temperature is more than Ms-50C, since the
martensite transformation is insufficient and as a result the tempered martensite is not
sufficiently formed, the desired metallic structure is not obtained. If desiring to utilize the
retained austenite for improving the ductility of the steel sheet, it is desirable to provide a lower
limit to the cooling stop temperature. Specifically, the cooling stop temperature is desirably
30 controlled to a range of Ms-50C to Ms-130C.
[0063]
The martensite transformation in the present invention occurs after the ferrite transformation
and bainite transformation. Along with the ferrite transformation and bainite transformation, C is
diffused in the austenite. For this reason, this does not match the Ms when heating to the
35 austenite single phase and rapidly cooling. The Ms in the present invention is found by
measuring the thermal expansion temperature in the second cooling. For example, the Ms in the
22
present invention can be found by using a Formastor tester or other apparatus able to measure
the amount of thermal expansion during continuous heat treatment, reproducing the heat cycle of
the hot dip galvanization line from the start of hot dip galvanization heat treatment
(corresponding to room temperature) to the above second cooling, and measuring the thermal
5 expansion temperature at that second cooling. However, in actual hot dip galvanization heat
treatment, sometimes cooling is stopped between Ms to room temperature, but at the time of
measurement of thermal expansion, cooling is performed down to room temperature. FIG. 2 is a
temperature-thermal expansion curve simulating by a thermal expansion measurement device a
heat cycle corresponding to the hot dip galvanization treatment according to an embodiment of
10 the present invention. Steel sheet linearly thermally contracts in the second cooling step, but
departs from a linear relationship at a certain temperature. The temperature at this time is the Ms
in the present invention.
[0064]
[Third soaking treatment: Holding in temperature region of 200C to 420C for 5 to 500
15 seconds]
After the second cooling, the steel sheet is reheated to a range of 200C to 420C for the
third soaking treatment. In this step, the martensite produced at the time of the second cooling is
tempered. If the holding temperature is less than 200C or the holding time is less than 5
seconds, the tempering does not sufficiently proceed. On the other hand, if the holding
20 temperature is more than 420C or if the holding time is more than 500 seconds, since the
martensite is excessively tempered and bainite transformation excessively proceeds, it becomes
difficult to obtain the desired strength and metallic structure. The temperature of the third
soaking treatment may be 240C or more and may be 400C or less. Further, the holding time
may be 15 seconds or more or may be 100 seconds or more and may be 400 seconds or less.
25 [0065]
After the third soaking treatment, the steel sheet is cooled down to room temperature to
obtain the final finished product. The steel sheet may also be skin pass rolled to correct the
flatness and adjust the surface roughness. In this case, to avoid deterioration of the ductility, the
elongation rate is preferably 2% or less.
30
EXAMPLES
[0066]
Next, examples of the present invention will be explained. The conditions in the examples
are illustrations of conditions employed for confirming the workability and effects of the present
35 invention. The present invention is not limited to these illustrations of conditions. The present
invention can employ various conditions so long as not deviating from the gist of the present
23
invention and achieving the object of the present invention.
[0067]
[Example A]
Steels having the chemical compositions shown in Table 1 were cast to prepare slabs. The
5 balance other than the constituents shown in Table 1 comprised Fe and impurities. These slabs
were hot rolled under the conditions shown in Table 2 to produce hot rolled steel sheets. After
that, the hot rolled steel sheets were pickled to remove the surface scale. After that, they were
cold rolled. Further, the obtained steel sheets were continuously hot dip galvanized under the
conditions shown in Table 2 and suitably treated for alloying. In the soaking treatments shown in
10 Table 2, the temperatures were held within a range of the temperatures shown in Table 2 10C.
The chemical compositions of the base steel sheets obtained by analyzing samples taken from
the produced hot dip galvanized steel sheets were equal with the chemical compositions of the
steels shown in Table 1.
[0068]
15 [Table 1-1]
24
Table 1-1
Steel type C Si Mn P S Al N O Cr Mo V Nb
A 0.215 1.77 2.27 0.005 0.0020 0.022 0.0029 0.0007
B 0.219 1.03 1.47 0.007 0.0024 0.747 0.0017 0.0015 0.67
C 0.187 0.78 2.52 0.009 0.0015 1.045 0.0026 0.0011
D 0.140 1.94 1.84 0.009 0.0022 0.028 0.0035 0.0004
E 0.205 1.93 2.52 0.008 0.0014 0.043 0.0019 0.0009 0.15 0.020
F 0.167 1.19 3.41 0.004 0.0007 0.275 0.0030 0.0006
G 0.202 1.49 2.66 0.009 0.0011 0.008 0.0029 0.0010
H 0.331 1.81 2.22 0.013 0.0021 0.045 0.0027 0.0007 0.41 0.28
I 0.275 1.97 3.28 0.018 0.0014 0.016 0.0041 0.0010
J 0.342 1.34 2.47 0.011 0.0008 0.490 0.0028 0.0012 0.38
K 0.090 1.07 2.20 0.009 0.0024 0.029 0.0037 0.0012 0.04
L 0.082 0.45 2.29 0.016 0.0021 0.053 0.0029 0.0011 0.29 0.07 0.010
M 0.111 0.77 2.47 0.014 0.0019 0.040 0.0041 0.0016 0.21 0.048
N 0.100 0.49 2.51 0.010 0.0009 0.007 0.0019 0.0008 0.53 0.11
O 0.156 0.21 2.85 0.007 0.0011 0.033 0.0028 0.0006
P 0.235 0.25 2.30 0.005 0.0019 0.040 0.0021 0.0011 0.23
Q 0.226 1.07 2.53 0.006 0.0019 0.052 0.0036 0.0021 0.40 0.013
R 0.041 1.60 2.68 0.019 0.0022 0.043 0.0028 0.0007
S 0.186 1.67 0.57 0.014 0.0007 0.052 0.0032 0.0013 0.54
T 0.147 1.12 4.45 0.009 0.0024 0.050 0.0016 0.0019
U 0.175 2.66 2.63 0.008 0.0015 0.033 0.0015 0.0020
V 0.379 1.70 2.22 0.011 0.0005 0.048 0.0031 0.0017
W 0.227 0.60 3.17 0.016 0.0024 1.859 0.0030 0.0019
Bold underlines show outside ranges of present invention.
Empty fields in table show corresponding constituents not intentionally added.
5 [0069]
[Table 1-2]
25
Table 1-2
Steel type Ti B Cu Ni Co W Sn Sb Others Ac1
A 750
B 0.017 0.0020 Bi:0.0065 748
C 719
D 760
E 0.027 0.0010 Ca:0.0043 752
F 0.24 0.17 718
G 0.0008 0.10 0.08 738
H 759
I 0.024 0.0021 Hf:0.0037,La:0.0050 745
J 0.39 736
K 0.030 0.0012 731
L Mg:0.0044 716
M 0.040 0.0010 Ce:0.0052,REM:0.010 719
N 0.010 0.0028 Zr:0.0079 720
O 699
P 0.021 0.0028 0.17 706
Q 0.026 0.0022 0.16 734
R 741
S 775
T 708
U 772
V 749
W 707
Bold underlines show outside ranges of present invention.
Empty fields in table show corresponding constituents not intentionally added.
5 [0070]
[Table 2-1]
26
Table 2-1
No. Steel
type
Continuous casting step Hot rolling step Cold rolling
step
Slab surface temp. at time
of end of secondary
cooling
C
Casting
rate
m/min
Slab
heating
temp.
C
Rough rolling total rolling
reduction at 1050C or
more
%
Finish inlet
side temp.
C
Finish exit
side temp.
C
Finish rolling total
rolling reduction
%
Coiling
temp.
C
Cold rolling
reduction
%
1 A 980 1.4 1250 85 980 890 91 610 53
2 A 940 1.1 1250 85 1010 910 91 560 53
3 A 890 1.3 1250 85 1030 950 91 580 53
4 A 400 1.6 1240 85 1010 930 91 580 53
5 A 940 0.1 1240 85 1010 920 91 560 53
6 A 900 1.3 1260 85 1030 930 91 530 53
7 A 990 1.3 1240 85 990 900 91 550 53
8 A 960 1.5 1270 85 1010 910 91 580 53
9 A 940 1.6 1240 85 1010 910 91 570 53
10 B 1030 1.1 1240 85 970 880 91 550 53
11 B 890 0.9 1270 85 1040 950 91 550 53
12 B 1000 1.1 1250 85 980 890 91 570 53
13 B 1000 1.5 1210 85 1020 940 91 560 53
14 B 960 3.6 1220 85 1030 940 91 560 53
15 B 970 0.9 1240 85 1010 930 91 570 53
16 C 1030 1.1 1280 85 1010 920 91 510 53
17 C 930 1.6 1250 85 1020 920 91 540 53
18 C 850 1.5 1270 85 1000 920 91 520 53
19 D 960 1.1 1210 85 1020 940 91 590 53
20 D 1010 0.9 1250 85 1000 910 91 580 53
Bold underlines show outside ranges of present invention.
[0071]
5 [Table 2-2]
27
Table 2-2
No. Steel
type
Continuous casting step Hot rolling step Cold rolling
step
Slab surface temp. at time of
end of secondary cooling
C
Casting rate
m/min
Slab heating
temp.
C
Rough rolling total rolling
reduction at 1050C or more
%
Finish inlet
side temp.
C
Finish exit
side temp.
C
Finish rolling total
rolling reduction
%
Coiling
temp.
C
Cold rolling
reduction
%
21 D 900 1.3 1210 85 1010 930 91 560 53
22 E 970 1.5 1210 85 1010 910 91 510 53
23 E 1180 1.2 1230 85 1000 920 91 570 53
24 E 1010 1.4 1280 85 1050 970 91 540 53
25 E 990 1.6 1260 85 1000 910 91 490 53
26 E 950 1.0 1250 85 1040 940 91 550 53
27 E 920 1.0 1270 85 1030 940 91 520 53
28 E 950 0.8 1240 85 970 890 91 530 53
29 E 910 0.8 1240 85 1010 930 91 520 53
30 F 910 1.4 1190 85 1050 970 91 510 53
31 F 1020 0.6 1240 85 1050 960 91 580 53
32 F 970 1.5 1230 85 1010 910 91 560 53
33 G 980 1.3 1260 85 1020 940 91 610 53
34 G 1030 1.5 1260 85 1010 920 91 520 53
35 H 970 1.5 1270 85 1020 920 91 620 53
36 H 970 1.6 1260 85 1020 920 91 600 53
37 I 970 0.9 1220 85 1020 920 91 600 53
38 I 900 1.6 1260 85 1010 910 91 580 53
39 J 970 1.6 1230 85 1050 960 91 580 53
40 J 940 1.3 1230 85 1040 960 91 550 53
Bold underlines show outside ranges of present invention.
[0072]
5 [Table 2-3]
28
Table 2-3
No. Steel
type
Continuous casting step Hot rolling step Cold rolling
step
Slab surface temp. at time of
end of secondary cooling
C
Casting
rate
m/min
Slab heating
temp.
C
Rough rolling total rolling
reduction at 1050C or more
%
Finish inlet
side temp.
C
Finish exit side
temp.
C
Finish rolling total
rolling reduction
%
Coiling temp.
C
Cold rolling
reduction
%
41 K 890 1.1 1260 85 980 900 91 550 53
42 K 950 1.6 1260 85 980 880 91 580 53
43 L 880 1.5 1260 85 1050 950 91 470 53
44 L 920 1.3 1250 85 1030 930 91 470 53
45 M 980 0.9 1260 85 1010 910 91 490 53
46 M 1010 0.9 1260 85 1020 920 91 490 53
47 N 1010 1.4 1220 85 1020 930 91 600 53
48 N 1030 0.8 1230 85 1020 930 91 620 53
49 O 940 1.0 1240 85 1000 920 91 580 53
50 O 940 1.2 1240 85 1000 920 91 550 53
51 P 1010 1.0 1220 85 1040 950 91 500 53
52 P 880 1.0 1210 85 1020 930 91 520 53
53 Q 910 0.9 1200 85 1000 920 91 620 53
54 Q 850 1.0 1210 85 1010 920 91 640 53
55 R 860 1.5 1250 85 1010 920 91 540 53
56 S 960 0.9 1240 85 1010 910 91 620 53
57 T 1020 1.5 1280 85 1040 940 91 610 53
58 U 930 1.0 1250 85 970 880 91 560 53
59 V 910 1.6 1250 85 1000 920 91 520 53
60 W 1010 0.9 1230 85 1020 940 91 530 53
Bold underlines show outside ranges of present invention.
[0073]
5 [Table 2-4]
29
Table 2-4
No.
Hot dip galvanizing step
Ms at hot dip galvanizing
step
C
Heating First soaking First
cooling
Second soaking Alloying Second
cooling
Third soaking
Heating rate from 650C to max. heating
temp.
C/s
Temp.
C
Holding
time
s
Cooling
rate
C/s
Temp.
C
Holding
time
s
Alloying
temp.
C
Cooling stop
temp.
C
Temp.
C
Holding
time
s
1 1.9 820 110 30 500 95 490 180 400 300 322
2 2.4 810 110 57 580 95 480 180 390 300 318
3 1.2 820 110 37 350 95 480 100 390 300 221
4 1.4 820 110 38 510 95 480 180 380 300 322
5 1.6 820 110 40 500 95 490 180 380 300 324
6 1.9 820 110 38 500 460 480 120 380 300 259
7 1.8 820 110 45 520 95 480 270 380 300 254
8 1.5 820 110 44 500 95 480 150 180 300 286
9 1.4 820 110 49 500 95 - 160 400 300 322
10 1.4 880 110 34 540 95 480 230 380 300 373
11 2.9 930 110 70 550 95 490 250 400 300 408
12 2.2 750 110 22 550 95 490 100 390 300 <50
13 2.3 860 110 2 550 95 480 150 400 300 242
14 1.9 870 110 51 540 95 490 220 400 300 389
15 1.9 860 110 40 550 95 - 230 380 300 350
16 1.8 890 110 31 560 95 500 200 380 300 331
17 2.2 890 110 33 490 790 460 80 400 300 <50
18 2.2 890 110 37 500 95 - 260 380 300 316
19 1.9 890 110 33 530 95 480 200 350 300 345
20 1.7 880 110 34 530 95 480 210 360 100 342
Bold underlines show outside ranges of present invention.
[0074]
5 [Table 2-5]
30
Table 2-5
No.
Hot dip galvanizing step
Ms at hot dip galvanizing
step
C
Heating First soaking First cooling Second soaking Alloying Second
cooling Third soaking
Heating rate from 650C to
max. heating temp.
C/s
Temp.
C
Holding
time
s
Cooling rate
C/s
Temp.
C
Holding
time
s
Alloying
temp.
C
Cooling stop
temp.
C
Temp.
C
Holding
time
s
21 1.8 880 110 32 640 95 480 150 350 300 239
22 1.4 860 110 36 550 95 520 220 390 300 358
23 1.9 870 110 42 550 95 510 230 390 300 345
24 1.7 900 110 39 550 95 540 230 400 300 374
25 1.6 850 110 30 550 95 500 210 300 300 356
26 1.5 850 110 35 550 95 550 350 400 300 342
27 1.6 880 110 39 550 60 510 230 400 300 366
28 1.4 870 110 57 550 95 500 230 390 3 327
29 2.0 860 110 41 560 95 - 190 400 300 361
30 2.2 850 110 36 540 95 500 230 400 300 355
31 1.4 850 110 47 590 95 590 240 400 480 356
32 2.2 850 110 37 550 95 - 180 400 300 356
33 1.8 830 110 31 550 95 500 200 400 300 349
34 1.4 830 110 44 550 95 - 200 400 300 349
35 2.1 880 110 30 530 95 510 240 400 300 334
36 1.5 880 110 26 530 95 - 240 400 300 334
37 1.5 870 110 30 540 95 530 200 350 300 322
38 2.2 870 110 50 540 95 - 200 350 300 322
39 1.2 870 110 43 550 95 520 200 370 300 333
40 2.1 870 110 39 550 95 - 200 380 300 335
Bold underlines show outside ranges of present invention.
[0075]
5 [Table 2-6]
31
Table 2-6
Bold underlines show outside ranges of present invention.
5
No.
Hot dip galvanizing step
Ms at hot dip galvanizing
step
C
Heating First soaking First
cooling Second soaking Alloying Second
cooling Third soaking
Heating rate from 650C to
max. heating temp.
C/s
Temp.
C
Holding
time
s
Cooling
rate
C/s
Temp.
C
Holding
time
s
Alloying
temp.
C
Cooling stop
temp.
C
Temp.
C
Holding time
s
41 1.9 820 110 43 550 95 540 60 300 20 409
42 1.9 820 110 37 550 95 - 60 300 20 409
43 1.2 820 110 28 540 95 530 90 280 20 407
44 1.8 820 110 24 540 95 - 90 280 20 406
45 2.0 820 110 34 550 95 530 70 280 20 397
46 1.9 820 110 27 550 95 - 70 280 20 398
47 1.2 810 110 36 550 95 540 50 300 20 395
48 1.6 810 110 41 550 95 - 50 300 20 395
49 1.7 810 110 38 540 95 500 50 300 20 363
50 1.7 810 110 46 560 95 - 50 300 20 365
51 1.8 850 110 34 560 95 510 120 280 20 375
52 2.2 850 110 37 560 95 - 120 280 20 375
53 1.9 860 110 29 550 95 530 100 290 20 361
54 1.7 860 110 25 550 95 - 100 290 20 361
55 2.0 880 110 35 540 95 510 250 390 330 417
56 1.5 880 110 43 550 95 500 100 400 330 <50
57 2.0 810 110 50 550 95 530 180 380 330 316
58 1.1 900 110 25 540 95 580 250 370 330 372
59 1.7 850 110 28 550 95 520 200 390 330 321
60 2.4 900 110 37 550 95 520 150 400 330 223
32
[0076]
A JIS No. 5 tensile test piece was taken from each of the thus obtained steel sheets in a
direction perpendicular to the rolling direction and was subjected to a tensile test based on JIS
Z2241: 2011 to measure the tensile strength (TS) and total elongation (El). Further, each test
5 piece was tested by the “JFS T 1001 Hole Expansion Test Method” of the Japan Iron and Steel
Federation Standards to measure the hole expansion rate (). A test piece with a TS of 980 MPa
or more and a TSEl
0 . 5 /1000 of 80 or more was judged good in mechanical properties and
as having press formability preferable for use as a member for automobiles.
[0077]
10 The low temperature toughness was evaluated by a Charpy test. A Charpy test piece was
obtained by stacking a plurality of steel sheets and bolting them together, confirming there was
no clearance between the steel sheets, then fabricating a depth 2 mm V-notched test piece. The
number of stacked steel sheets was set so that the thickness of the test piece after stacking
became the closest to 10 mm. For example, if the thickness is 1.2 mm, eight are stacked to give a
15 thickness of the test piece of 9.6 mm. The stacked Charpy test piece was obtained using the sheet
width direction as the long direction. A low temperature toughness when the test temperature
was -50C and +20C and the impact absorption energy ratio vE- 5 0 /vE2 0 at -50C and +20C
was 0.6 or more was judged to be excellent (in Table 3, “very good”). The conditions other than
the above were based on JIS Z 2242: 2018.
20 [0078]
Furthermore, the thus obtained steel sheets were examined for microstructures. The
procedures for examination of the microstructures were as explained above.
[0079]
The results are shown in Table 3. In Table 3, “GA” means hot dip galvannealing, while GI
25 means hot dip galvanizing without alloying treatment. The “number ratio satisfying formulas (1)
and (2)” in Table 3 is obtained by following the method of measurement explained previously in
this Description to measure in particular 10 different particles of tempered martensite.
[0080]
[Table 3-1]
33
Table 3-1
No. Steel
type Coating
Microstructure Mechanical properties
Ferrite Remarks
%
Retained
austenite
%
Tempered
martensite
%
Fresh
martensite
%
Pearlite+
cementite
%
Bainite
%
No. density
satisfying
formulas (1)
and (2)
Press formability
vE-50/
vE20
TS
MPa
El
%

%
TSEl
0.5
/1000
1 A GA 31 13 30 3 0 23 0.5 1028 24.5 31 140 Very good Ex.
2 A GA 36 11 34 2 0 17 0.7 1077 21.3 42 149 Very good Ex.
3 A GA 30 11 15 2 0 42 0.1 1006 22.0 39 138 Poor Comp. ex.
4 A GA 32 12 33 2 0 21 0.1 1003 22.4 38 138 Poor Comp. ex.
5 A GA 30 11 37 2 0 20 0.1 1059 22.5 42 153 Poor Comp. ex.
6 A GA 33 12 18 1 0 36 0.6 988 23.6 29 127 Very good Ex.
7 A GA 34 9 0 9 0 48 - 949 20.3 16 77 Very good Comp. ex.
8 A GA 33 5 19 20 0 23 0.7 1126 17.1 15 74 Poor Comp. ex.
9 A GI 32 12 33 2 0 21 0.7 1022 24.0 33 141 Very good Ex.
10 B GA 33 11 36 2 0 18 0.8 1044 21.7 35 134 Very good Ex.
11 B GA 8 10 56 2 0 24 0.8 1120 17.2 58 147 Very good Ex
12 B GA 75 6 0 8 0 11 - 803 23.1 30 101 Very good Comp. ex.
13 B GA 66 5 5 5 7 12 0.7 913 19.2 19 76 Very good Comp. ex.
14 B GA 22 10 40 2 0 26 0.1 1057 20.6 33 125 Poor Comp. ex.
15 B GI 40 11 21 2 0 26 0.8 1029 23.7 28 129 Very good Ex.
16 C GA 47 10 23 3 0 17 0.8 1004 22.8 18 97 Very good Ex.
17 C GA 48 11 0 5 0 36 - 918 20.7 20 86 Very good Comp. ex.
18 C GI 45 11 10 5 0 29 0.8 988 23.9 16 94 Very good Ex.
19 D GA 15 7 50 1 0 27 0.7 1067 17.7 51 135 Very good Ex.
20 D GA 20 7 49 3 0 21 0.7 1103 19.0 44 139 Very good Ex.
Bold underlines show outside ranges of present invention.
[0081]
5 [Table 3-2]
34
Table 3-2
No. Steel
type Coating
Microstructure Mechanical properties
Ferrite Remarks
%
Retained
austenite
%
Tempered
martensite
%
Fresh
martensite
%
Pearlite+
cementite
%
Bainite
%
No. density
satisfying
formulas (1)
and (2)
Press formability
vE-50/
vE20
TS
MPa
El
%

%
TSEl
0.5
/1000
21 D GA 66 7 10 2 6 9 0.1 922 18.6 20 77 Poor Comp. ex.
22 E GA 17 11 48 2 0 22 0.9 1207 17.1 48 143 Very good Ex.
23 E GA 14 12 45 2 0 27 0.1 1234 16.5 51 145 Poor Comp. ex.
24 E GA 0 9 65 1 0 25 0.9 1279 14.4 62 145 Very good Ex.
25 E GA 21 5 62 3 0 9 0.9 1314 13.5 38 109 Very good Ex.
26 E GA 23 7 0 20 0 50 - 1256 13.9 19 77 Poor Comp. ex.
27 E GA 12 12 51 1 0 24 0.1 1254 16.5 40 131 Poor Comp. ex.
28 E GA 18 4 36 19 0 23 0.7 1377 12.2 15 65 Poor Comp. ex.
29 E GI 18 10 60 2 0 10 0.8 1201 17.6 44 140 Very good Ex.
30 F GA 4 8 60 1 0 27 0.9 1215 14.5 51 126 Very good Ex.
31 F GA 4 7 64 3 0 22 0.7 1228 14.3 40 111 Very good Ex.
32 F GI 4 8 75 1 0 12 0.8 1267 13.1 55 123 Very good Ex.
33 G GA 20 12 42 2 0 24 0.8 1203 18.2 41 139 Very good Ex.
34 G GI 20 12 42 1 0 25 1.0 1195 16.7 42 129 Very good Ex.
35 H GA 0 24 60 4 0 12 0.5 1479 17.7 24 128 Very good Ex.
36 H GI 0 24 60 4 0 12 0.6 1486 18.0 27 139 Very good Ex.
37 I GA 0 18 62 3 0 17 0.9 1478 15.4 31 127 Very good Ex.
38 I GI 0 18 63 3 0 16 0.7 1461 15.0 33 126 Very good Ex.
39 J GA 6 26 54 4 0 10 0.8 1567 17.2 30 149 Very good Ex.
40 J GI 5 25 58 3 0 9 0.6 1554 16.2 30 138 Very good Ex.
Bold underlines show outside ranges of present invention.
[0082]
5 [Table 3-3]
35
Table 3-3
No. Steel
type Coating
Microstructure Mechanical properties
Ferrite Remarks
%
Retained
austenite
%
Tempered
martensite
%
Fresh
martensite
%
Pearlite+
cementite
%
Bainite
%
No. density
satisfying
formulas (1)
and (2)
Press formability
vE-50/
vE20
TS
MPa
El
%

%
TSEl
0.5
/1000
41 K GA 38 2 33 5 0 22 0.7 1012 13.6 51 98 Very good Ex.
42 K GI 38 2 35 5 0 20 0.7 1019 13.7 50 98 Very good Ex.
43 L GA 30 1 31 3 0 35 0.6 1004 14.0 50 99 Very good Ex.
44 L GI 30 1 30 3 0 36 0.9 992 14.2 48 98 Very good Ex.
45 M GA 15 2 53 6 0 24 0.8 1260 11.0 49 97 Very good Ex.
46 M GI 15 2 54 6 0 23 0.9 1246 11.2 46 95 Very good Ex.
47 N GA 17 0 58 4 0 21 0.8 1223 10.9 52 96 Very good Ex.
48 N GI 17 0 59 4 0 20 0.8 1241 10.8 53 98 Very good Ex.
49 O GA 22 2 50 2 0 24 0.8 1223 11.2 36 82 Very good Ex.
50 O GI 20 2 53 2 0 23 0.8 1232 10.6 38 81 Very good Ex.
51 P GA 0 2 84 3 0 11 0.8 1547 8.1 47 86 Very good Ex.
52 P GI 0 2 85 3 0 10 0.8 1552 8.0 50 88 Very good Ex.
53 Q GA 0 4 80 6 0 10 0.7 1536 9.0 44 91 Very good Ex.
54 Q GI 0 4 80 6 0 10 0.6 1545 9.1 46 95 Very good Ex.
55 R GA 35 2 34 0 0 29 0.6 824 24.9 59 158 Very good Comp. ex.
56 S GA 70 10 0 0 0 20 - 757 25.6 40 123 Very good Comp. ex.
57 T GA 14 3 57 15 0 11 0.9 1412 10.0 10 45 Poor Comp. ex.
58 U GA 13 7 45 16 0 19 0.8 1367 10.3 11 47 Poor Comp. ex.
59 V GA 0 32 35 11 0 22 0.6 1382 23.1 13 113 Poor Comp. ex.
60 W GA 60 10 9 4 0 17 0.5 940 26.2 21 114 Very good Comp. ex.
Bold underlines show outside ranges of present invention.
36
[0083]
Comparative Examples 3 and 21 had temperatures of the second soaking treatment in the
hot dip galvanizing step of respectively less than 480C and more than 600C. As a result, the
ratios of tempered martensite satisfying the formulas (1) and (2) became less than 0.2 and the
5 low temperature toughnesses were poor. Comparative Examples 4 and 23 had surface slab
temperatures at the time of the end of the secondary cooling of the continuous casting step of
respectively less than 500C and more than 1100C. As a result, the ratios of tempered
martensite satisfying the formulas (1) and (2) became less than 0.2 and the low temperature
toughnesses were poor. Comparative Examples 5 and 14 had casting rates in the continuous
10 casting step of respectively less than 0.4 m/min and more than 3.0 m/min. As a result, the ratios
of tempered martensite satisfying the formulas (1) and (2) became less than 0.2 and the low
temperature toughnesses were poor. Comparative Example 7, 12, 17, and 26 had stop
temperatures of the second cooling in the hot dip galvanizing step of more than Ms-50C and a
tempered martensite not satisfying 5%. Further, Comparative Example 26 had a fresh martensite
15 of more than 10%. As a result, Comparative Examples 7, 12, and 17 had tensile strengths of less
than 980 MPa. Comparative Example 26 contained hard fresh martensite in large amounts, so
while the tensile strength was secured, the press formability and low temperature toughness
became poor. Comparative Example 8 had a temperature of the third soaking treatment in the hot
dip galvanizing step was less than 200C. As a result, the fresh martensite became more than
20 10% and the press formability and low temperature toughness were poor.
[0084]
Comparative Example 13 had an average cooling rate of the first cooling in the hot dip
galvanizing step of less than 10C/s. As a result, the ferrite became more than 50%, the total of
the pearlite and cementite became more than 5%, and the press formability was poor.
25 Comparative Example 27 had a holding time of the second soaking treatment in the hot dip
galvanizing step of less than 80 seconds. As a result, the ratio of the tempered martensite
satisfying the formulas (1) and (2) became less than 0.2 and the low temperature toughness was
poor. Comparative Example 28 had a holding time of the third soaking treatment in the hot dip
galvanizing step of less than 5 seconds. As a result, the fresh martensite became more than 10%
30 and the press formability and low temperature toughness were poor. Comparative Examples 55
to 60 had chemical compositions of not controlled to within predetermined ranges, so the desired
metallic structure was not obtained and the press formability and/or low temperature toughness
were poor.
[0085]
35 In contrast to this, the hot dip galvanized steel sheets of the examples have a tensile strength
of 980 MPa or more and TSEl
0 . 5 /1000 of 80 or more and further have a vE- 5 0 /vE2 0 of
37
0.6 or more, so it is learned that they are excellent in press formability and low temperature
toughness.
[0086]
[Example B]
5 In this example, the inventors studied the presence or absence of a specific soaking
treatment. First, they prepared a slab having the chemical composition shown in Table 1, then, as
shown in Table 4, made the first cooling gradual cooling to eliminate the second soaking
treatment. Other than that, the same procedure was followed as the case of Example A to obtain
hot dip galvanized steel sheet. The steel structures and mechanical properties in the obtained hot
10 dip galvanized steel sheet were investigated by methods similar to the case of Example A. The
results are shown in Table 5. In the different soaking treatments shown in Table 4, the
temperature was maintained within a range of the temperature shown in Table 4 10C.
[0087]
[Table 4]
38
Table 4
No. Steel
type
Continuous casting
step Hot rolling step Cold rolling
step Hot dip galvanizing step
Ms at hot dip
galvanizing step
Slab surface
temp. at
secondary
cooling end
point
Casting
rate
Slab
heating
temp.
Rough rolling
total rolling
reduction at
1050C
or more
Finish inlet
side temp.
Finish exit
side temp.
Finish rolling
total rolling
reduction
Coiling
temp.
Cold rolling
reduction
Heating First soaking First cooling Alloying Third soaking
Heating rate
from 650C
to maximum
heating temp.
Temp. Holding
time
Cooling
rate
Cooling
stop
temp
Alloying
temp. Temp. Holding
time
C m/min C % C C % C % C/s C s C/s C C C s C
61 A 980 1.4 1250 85 980 890 91 610 53 1.9 820 110 1 180 490 400 300 255
Bold underlines show outside ranges of present invention.
[0088]
5 [Table 5]
Table 5
No. Steel
type Coating
Microstructure Mechanical properties
Ferrite Remarks
%
Retained
austenite
%
Tempered
martensite
%
Fresh
martensite
%
Pearlite+
cementite
%
Bainite
%
No. density
satisfying formulas
(1) and (2)
Press formability
TS vE-50/vE20
MPa
El
%

%
TSEl
0.5
/1000
61 A GA 53 7 12 6 6 16 0.1 902 18.7 20 75 Poor Comp. ex.
Bold underlines show outside ranges of present invention.
39
[0089]
As clear from the results of Table 5, if making the first cooling gradual cooling to eliminate
second soaking treatment, the desired metallic structure cannot be obtained, the ratio of the
tempered martensite satisfying the formulas (1) and (2) became less than 2.0, and the press
5 formability and low temperature toughness were poor.
[0090]
[Example C]
In this example, the inventors similarly studied the relationship of the soaking treatment and
coating treatment. First, they prepared a slab having the chemical composition shown in Table 1,
10 then, as shown in Table 6, performed the same procedure as the case of Example A to obtain hot
dip galvanized steel sheet except for performing the coating and alloying treatment not after the
second soaking treatment but after the third soaking treatment. The steel structures and
mechanical properties in the obtained hot dip galvanized steel sheet were investigated by
methods similar to the case of Example A. The results are shown in Table 7. In the different
15 soaking treatments shown in Table 6, the temperature was maintained within a range of the
temperature shown in Table 6 10C.
[0091]
[Table 6]
40
Table 6
No. Steel
type
Continuous casting
step Hot rolling step Cold rolling
step Hot dip galvanizing step
Ms at hot dip
galvanizing
step
Slab surface
temp. at
secondary
cooling end
point
Casting
rate
Slab
heating
temp.
Rough
rolling total
rolling
reduction at
1050C
or more
Finish inlet
side temp.
Finish exit
side temp.
Finish
rolling total
rolling
reduction
Coiling
temp.
Cold rolling
reduction
Heating First soaking First
cooling
Second
soaking
Second
cooling Third soaking Alloying
Heating rate
from 650C
to maximum
heating
temp.
Temp. Holding
time
Cooling
rate Temp. Holding
time
Cooling
stop
temp.
Temp. Holding
time
Alloying
temp.
C m/min C ％ C C ％ C ％ C/s C s C/s C s C C s C C
63 A 980 1.4 1250 85 980 890 91 610 53 1.9 820 110 30 500 95 180 400 300 500 322
Bold underlines show outside ranges of present invention.
[0092]
5 [Table 7]
Table 7
No. Steel
type Coating
Microstructure Mechanical properties
Ferrite Remarks
%
Retained
austenite
%
Tempered
martensite
%
Fresh
martensite
%
Pearlite+
cementite
%
Bainite
%
No. density
satisfying
formulas (1) and
(2)
Press formability
TS vE-50/vE20
MPa
El
%

%
TSEl
0.5
/1000
63 A GA 32 8 30 6 7 17 0.5 966 19.3 17 77 Poor Comp. ex.
Bold underlines show outside ranges of present invention.
41
[0093]
As clear from the results of Table 7, if performing the coating and alloying treatment after
the third soaking treatment, the desired metallic structures cannot be obtained and the press
formability and low temperature toughness were poor.

CLAIMS

[Claim 1]A hot dip galvanized steel sheet comprising a base steel sheet and a hot dip galvanized layer
5 on at least one surface of the base steel sheet, wherein the base steel sheet has a chemical
composition comprising, by mass%,
C: 0.050% to 0.350%,
Si: 0.10% to 2.50%,
Mn: 1.00% to 3.50%,
10 P: 0.050% or less,
S: 0.0100% or less,
Al: 0.001% to 1.500%,
N: 0.0100% or less,
O: 0.0100% or less,
15 Ti: 0% to 0.200%,
B: 0% to 0.0100%,
V: 0% to 1.00%,
Nb: 0% to 0.100%,
Cr: 0% to 2.00%,
20 Ni: 0% to 1.00%,
Cu: 0% to 1.00%,
Co: 0% to 1.00%,
Mo: 0% to 1.00%,
W: 0% to 1.00%,
25 Sn: 0% to 1.00%,
Sb: 0% to 1.00%,
Ca: 0% to 0.0100%,
Mg: 0% to 0.0100%,
Ce: 0% to 0.0100%,
30 Zr: 0% to 0.0100%,
La: 0% to 0.0100%,
Hf: 0% to 0.0100%,
Bi: 0% to 0.0100%,
REM other than Ce and La: 0% to 0.0100% and
35 a balance of Fe and impurities,
a steel microstructure at a range of 1/8 thickness to 3/8 thickness centered about a position
43
of 1/4 thickness from a surface of the base steel sheet contains, by volume fraction,
ferrite: 0% to 50%,
retained austenite: 0% to 30%,
tempered martensite: 5% or more,
5 fresh martensite: 0% to 10%, and
pearlite and cementite in total: 0% to 5%,
when there are remaining structures, the remaining structures consist of bainite, and
a number ratio of tempered martensite with a Mn concentration profile satisfying the
following formulas (1) and (2) is 0.2 or more with respect to the total number of the tempered
10 martensite:
[Mn]b /[Mn]a >1.2  (1)
[Mn]a /[Mn]<2.0  (2)
where [Mn] is the Mn content (mass%) in the base steel sheet, [Mn]a is the average Mn
concentration (mass%) in the tempered martensite, and [Mn]b is the Mn concentration (mass%)
15 at the interfaces of different phases of the tempered martensite and ferrite phase and bainite
phase.
[Claim 2]
The hot dip galvanized steel sheet according to claim 1, wherein the steel microstructure
20 further contains, by volume fraction, retained austenite: 6% to 30%.
[Claim 3]
A method for producing the hot dip galvanized steel sheet according to claim 1 or 2,
comprising a continuous casting step for continuously casting a slab having the chemical
25 composition according to claim 1, a hot rolling step for hot rolling the cast slab, and a hot dip
galvanizing step for hot dip galvanizing the obtained steel sheet, wherein
(A) the continuous casting step satisfies the conditions of the following (A1) and (A2):
(A1) a slab surface temperature at the time of the end of a secondary cooling is 500 to
1100C and
30 (A2) a casting rate is 0.4 to 3.0 m/s, and
(B) the hot dip galvanizing step comprises heating the steel sheet to first soak it, first
cooling then second soaking the first soaked steel sheet, dipping the second soaked steel sheet in
a hot dip galvanizing bath, second cooling the coated steel sheet, and heating the second cooled
steel sheet then third soaking it, and further satisfies the conditions of the following (B1) to (B6):
35 (B1) in the heating of the steel sheet before the first soaking, the average heating rate
from 650C to a maximum heating temperature of Ac1+30C or more and 950C or less is
44
0.5C/s to 10.0C/s,
(B2) the steel sheet is held at the maximum heating temperature for 1 second to 1000
seconds (first soaking),
(B3) an average cooling rate in a temperature range of 700 to 600C at the first cooling
5 is 10 to 100C/s,
(B4) the first cooled steel sheet is held in a range of 480 to 600C for 80 seconds to 500
seconds (second soaking),
(B5) the second cooling is performed down to Ms-50C or less, and
(B6) the second cooled steel sheet is heated to a temperature region of 200 to 420C,
10 then held in the temperature region for 5 to 500 seconds (third soaking).