U.S. patent application number 16/337261 was filed with the patent office on 2019-07-25 for steel plate.
This patent application is currently assigned to NIPPON STEEL & SUMITOMO METAL CORPORATION. The applicant listed for this patent is NIPPON STEEL & SUMITOMO METAL CORPORATION. Invention is credited to Norimasa KAWABATA, Takumi MIYAKE, Naoki SAITOH, Mitsuru SAWAMURA, Yasunori TAKAHASHI, Takeshi TSUZUKI.
Application Number | 20190226066 16/337261 |
Document ID | / |
Family ID | 64735536 |
Filed Date | 2019-07-25 |
United States Patent
Application |
20190226066 |
Kind Code |
A1 |
SAWAMURA; Mitsuru ; et
al. |
July 25, 2019 |
STEEL PLATE
Abstract
A steel plate according to an aspect of the present invention
has a predetermined chemical composition, an index Q obtained by
Equation (1) is 0.00 or more, a carbon equivalent Ceq (%) obtained
by Equation (2) is less than 0.800%, a ratio of a difference
between a hardness at a surface layer portion and a hardness at a
thickness center portion to the hardness at the surface layer
portion at a room temperature is 15.0% or less, the hardness at the
suffice layer portion at a room temperature is 400 or more in terms
of Vickers hardness, and a steel thickness is 40 or more.
Q=0.18-1.3(logT)+0.75(2.7.times.[C]+[Mn]+0.45.times.[Ni]+0.8.times.[Cr]+-
2.times.[Mo]) (1)
Ceq(%)=[C]+[Mn]/6+[Si]/24+[Ni]/40+[Cr]/5+[Mo]/4+[V]/4 (2)
Inventors: |
SAWAMURA; Mitsuru; (Tokyo,
JP) ; SAITOH; Naoki; (Tokyo, JP) ; TAKAHASHI;
Yasunori; (Tokyo, JP) ; MIYAKE; Takumi;
(Tokyo, JP) ; KAWABATA; Norimasa; (Tokyo, JP)
; TSUZUKI; Takeshi; (Tokyo, JP) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
NIPPON STEEL & SUMITOMO METAL CORPORATION |
Tokyo |
|
JP |
|
|
Assignee: |
NIPPON STEEL & SUMITOMO METAL
CORPORATION
Tokyo
JP
|
Family ID: |
64735536 |
Appl. No.: |
16/337261 |
Filed: |
February 27, 2018 |
PCT Filed: |
February 27, 2018 |
PCT NO: |
PCT/JP2018/007161 |
371 Date: |
March 27, 2019 |
Current U.S.
Class: |
1/1 |
Current CPC
Class: |
C21D 8/02 20130101; C21D
6/008 20130101; C22C 38/00 20130101; C22C 38/46 20130101; C22C
38/50 20130101; C21D 6/002 20130101; C22C 38/22 20130101; C22C
38/24 20130101; C21D 2211/001 20130101; C21D 6/005 20130101; C22C
38/005 20130101; C22C 38/26 20130101; C22C 38/001 20130101; C22C
38/42 20130101; C22C 38/18 20130101; C22C 38/58 20130101; C21D 9/46
20130101; C22C 38/48 20130101; C22C 38/28 20130101; C22C 38/54
20130101; C21D 8/0263 20130101; C22C 38/44 20130101; C21D 8/0205
20130101; C22C 38/38 20130101; C21D 8/0226 20130101; C22C 38/06
20130101; C22C 38/04 20130101; C22C 38/002 20130101; C22C 38/32
20130101; C22C 38/02 20130101 |
International
Class: |
C22C 38/58 20060101
C22C038/58; C21D 9/46 20060101 C21D009/46; C21D 8/02 20060101
C21D008/02; C21D 6/00 20060101 C21D006/00; C22C 38/54 20060101
C22C038/54; C22C 38/50 20060101 C22C038/50; C22C 38/48 20060101
C22C038/48; C22C 38/46 20060101 C22C038/46; C22C 38/42 20060101
C22C038/42; C22C 38/06 20060101 C22C038/06; C22C 38/04 20060101
C22C038/04; C22C 38/02 20060101 C22C038/02; C22C 38/00 20060101
C22C038/00; C22C 38/44 20060101 C22C038/44 |
Foreign Application Data
Date |
Code |
Application Number |
Jun 21, 2017 |
JP |
2017-121641 |
Claims
1. A steel plate comprising, as a chemical composition, by mass %:
C: 0.20% to 0.35%; Si: more than 1.00% to 2.00%; Mn: 0.60% to
2.00%; Cr: 0.10% to 2.00%; Mo: 0.05% to 1.00%; Al: 0.010% to
0.100%; N: 0.0020% to 0.0100%; B: 0.0003% to 0.0020%; P: 0.0200% or
less; S: less than 0.0100%; Cu: 0% to 0.500%; Ni: 0% to 1.00%; Nb:
0% to 0.050%; V: 0% to 0.120%; Ti: 0% to 0.025%; Ca: 0% to 0.050%;
Mg: 0% to 0.050%; REM: 0% to 0.100%; and a remainder consisting of
Fe and impurities, wherein an index Q obtained by Equation (1) is
0.00 or more, a carbon equivalent Ceq (%) obtained by Equation (2)
is less than 0.800%, a ratio of a difference between a hardness at
a surface layer portion and a hardness at a thickness center
portion to the hardness at the surface layer portion at a room
temperature is 15.0% or less and the hardness at the surface layer
portion at a room temperature is 400 or more in terms of Vickers
hardness, and a steel thickness T is 40 mm or more,
Q=0.18-1.3(logT)+0.75(2.7.times.[C]+[Mn]+0.45.times.[Ni]+0.8.times.[Cr]+2-
.times.[Mo]) (1)
Ceq(%)=[C]+[Mn]/6+[Si]/24+[Ni]/40+[Cr]/5+[Mo]/4+[V]/4 (2) where the
index Q of Equation (1) is calculated by substituting a numerical
value of the steel thickness T (mm), a numerical value of an amount
[X] of each element X in terms of mass % and 0 in a case where the
element X is not contained, the carbon equivalent Ceq (%) of
Equation (2) is calculated by substituting a numerical value of an
amount [X] of each element X in terms of mass % and 0 in a case
where the element X is not contained.
2. The steel plate according to claim 1, wherein the index Q is
0.04 or more, and the ratio is 13.0% or less.
3. The steel plate according to claim 1 or 2, comprising, as the
chemical composition, by mass %, Ni is 0.05% to 1.00%.
4. The steel plate according to claim 1 or 2, comprising, as the
chemical composition, by mass %, Mn is 0.63% to 2.00%.
5. The steel plate according to claim 3, comprising, as the
chemical composition, by mass %, Mn is 0.63% to 2.00%.
6. A steel plate comprising, as a chemical composition, by mass %:
C: 0.20% to 0.35%; Si: more than 1.00% to 2.00%; Mn: 0.60% to
2.00%; Cr: 0.10% to 2.00%; Mo: 0.05% to 1.00%; Al: 0.010% to
0.100%; N: 0.0020% to 0.0100%; B: 0.0003% to 0.0020%; P: 0.0200% or
less; S: less than 0.0100%; Cu: 0% to 0.500%; Ni: 0% to 1.00%; Nb:
0% to 0.050%; V: 0% to 0.120%; Ti: 0% to 0.025%; Ca: 0% to 0.050%;
Mg: 0% to 0.050%; REM: 0% to 0.100%; and a remainder comprising Fe
and impurities, wherein an index Q obtained by Equation (1) is 0.00
or more, a carbon equivalent Ceq (%) obtained by Equation (2) is
less than 0.800%, a ratio of a difference between a hardness at a
surface layer portion and a hardness at a thickness center portion
to the hardness at the surface layer portion at a room temperature
is 15.0% or less and the hardness at the surface layer portion at a
room temperature is 400 or more in terms of Vickers hardness, and a
steel thickness T is 40 mm or more,
Q=0.18-1.3(logT)+0.75(2.7.times.[C]+[Mn]+0.45.times.[Ni]+0.8.times.[Cr]+2-
.times.[Mo]) (1)
Ceq(%)=[C]+[Mn]/6+[Si]/24+[Ni]/40+[Cr]/5+[Mo]/4+[V]/4 (2) where the
index Q of Equation (1) is calculated by substituting a numerical
value of the steel thickness T (mm), a numerical value of an amount
[X] of each element X in terms of mass % and 0 in a case where the
element X is not contained, the carbon equivalent Ceq (%) of
Equation (2) is calculated by substituting a numerical value of an
amount [X] of each element X in terms of mass % and 0 in a case
where the element X is not contained.
Description
TECHNICAL FIELD OF THE INVENTION
[0001] The present invention relates to a steel plate
(wear-resistant steel plate) having excellent wear resistance.
[0002] Priority is claimed on Japanese Patent Application No.
2017-121641, filed on Jun. 21, 2017the content of which is
incorporated herein by reference.
RELATED ART
[0003] For applications such as construction machines and
industrial machines, a wear-resistant steel plate that can be used
over a long period of time is required even under a severe wear
environment, and from the viewpoint of securing, a wear margin due
to an increase in steel thickness, an improvement in wear
resistance is required. In general, in order to improve the wear
resistance of a steel plate, it is necessary to increase the
hardness of the steel plate. Particularly in a thick wear-resistant
steel plate having a steel thickness of 40 mm or more, an object
thereof is to secure not only the hardness in the vicinity of the
surface of the steel plate (hereinafter, sometimes referred to as
"hardness at a surface layer portion", and a surface layer portion
is a region of 1 mm to 5 mm from the surface of the steel plate in
the through-thickness direction) but also the hardness in the
center portion in the through-thickness direction (hereinafter,
sometimes referred to as "hardness at a thickness center portion",
and the center portion is a region of .+-.5 mm (10 mm in total
thickness) from a position (that is, the center of the steel
thickness) away from the surface of the steel plate by 1/2 of the
steel thickness T (that is, T/2) in the through-thickness
direction) in which it is difficult to obtain hardness.
[0004] Since wear-resistant steel plates are locally exposed to a
temperature higher than a room temperature and sometimes used under
severe environments, there may be cases where the wear-resistant
steel plates are required to have a small decrease in hardness
(excellent high-temperature hardness) even in a temperature range
higher than a room temperature (for example, a temperature range of
about 150.degree. C. to 300.degree. C.). Steel plates in which the
Si content is increased to secure hardness in a temperature range
higher than a room temperature (hereinafter, sometimes referred to
as "high-temperature hardness") have been proposed (for example,
refer to Patent Documents 1 to 3).
PRIOR ART DOCUMENT
Patent Documents
[0005] [Patent Document 1] Japanese Unexamined Patent Application,
First Publication No. H8-41535
[0006] [Patent Document 2] Japanese Unexamined Patent Application,
First Publication. No. 2001-49387
[0007] [Patent Document 3] Japanese Unexamined Patent Application,
First Publication No. 2002-235144
DISCLOSURE OF THE INVENTION
Problems to be Solved by the Invention
[0008] For example, Patent Document 1 proposes a steel plate having
a Si content of 0.40 to 1.50 mass % (hereinafter, "mass %" is
simply referred to as "%") and containing Nb. However, in Patent
Document 1, the steel thickness of the steel plate is 40 mm or
less, the hardness at the thickness center portion thereof is not
described, and there is no examination from the viewpoint of
securing a wear margin due to an increase in the thickness of the
steel plate.
[0009] In Patent Document 2, a severe wear environment locally
exposed to a temperature higher than a room temperature is
postulated, and a steel which contains Si in an amount of more than
0.5% to 1.2% in order to secure the high-temperature hardness of
the steel and uses precipitation strengthening caused by V carbide
is proposed. However the steel containing a large amount of V is
liable to cause cracking of cast pieces, and there is concern of a
decrease in manufacturability.
[0010] Patent Document 3 proposes a steel plate containing 1.00%)
to 1.50% of Si in order to secure the high-temperature hardness of
the steel plate. In Patent Document 3, it is considered to secure
the hardness at the thickness center portion of the steel plate.
However, the difference between the hardness at the surface layer
portion and the hardness at the thickness center portion
(hereinafter, sometimes referred to as "hardness difference between
the surface layer portion and the thickness center portion", or
simply "hardness difference") is not described, and there is no
examination from the viewpoint of securing a wear margin due to an
increase in the thickness of the steel plate.
[0011] Considering the use environment and use form of a
wear-resistant steel plate, there may be cases where maintenance of
a high hardness even not only at a room temperature but also in a
high-temperature environment at about 150.degree. C. to 300.degree.
C., and a sufficient hardness for the center portion in the
through-thickness direction (thickness center portion) are
required. Although the hardness at the thickness center portion can
be easily secured by increasing the amounts of alloying elements,
due to a decrease in weldability, the upper limit of a carbon
equivalent needs to be provided. In order to secure the hardness of
the steel plate in a high-temperature environment, addition of Si
in an amount of more than 1.00% is considered to be effective.
However, the inventors found that in a steel plate containing Si in
an amount of more than 1.00%, there is a tendency toward a
significant increase in the difference between the hardness at the
surface layer portion and the hardness at the thickness center
portion, which is not preferable regarding the wear resistance of
the steel plate.
[0012] There has been no report on the relationship between the
steel plate containing Si in an amount of more than 1.00% and the
hardness difference, and there have been insufficient examinations
for reducing the hardness difference at a room temperature. The
present invention has been made taking the foregoing circumstances
into consideration, and an object thereof is to provide a steel
plate having excellent wear resistance, in which high hardness can
be maintained even in a high-temperature environment as well as at
a room temperature, the carbon equivalent of a steel plate
particularly having a steel thickness of 40 mm or more is set to be
less, than 0.800%, and the difference between a hardness at a
surface layer portion and a hardness at a thickness center portion
at a room temperature is set to 15.0% or less of the hardness at
the surface layer portion.
Means for Solving the Problem
[0013] Steels containing Si in an amount of more than 1.00% to
2.00% are advantageous in terms of wear resistance because hardness
can be secured at a room temperature and high temperatures. On the
other hand, it was found by the examinations of the inventors that
in a steel plate containing Si in an amount of more than 1.00% and
having a steel thickness of 40 mm or more, a difference between a
hardness at a surface layer portion and a hardness at a thickness
center portion is likely to occur at a room temperature. This is
because the cooling rate at the center portion of the steel plate
in the through-thickness direction is lower than that at the
surface and surface layer portion, and a martensite structure is
insufficiently formed. However, the influence of an increase in the
Si content is not necessarily clear.
[0014] As a further examination, the inventors derives an index Q
for reducing the difference between a hardness at a surface layer
portion and a hardness at a thickness center portion at a room
temperature in a steel plate having a steel thickness of 40 mm or
more and containing Si in an amount of more than 1.00%. The index Q
is obtained by Equation (1) in which the hardenability of alloying
elements and the steel thickness are considered. However, in
Equation (1), since attention is paid to the alloying elements (C,
Mn, Ni, Cr, and Mo) other than Si, which are necessary to reduce
the difference between the hardness, at the surface layer portion
and the hardness at the thickness center portion of the steel plate
containing Si in an amount of more than 1.00%, the amount of Si is
not considered. In the following description, the hardness at a
room temperature is sometimes referred to as "a room-temperature
hardness". In the following, simply "hardness" represents hardness
at a room temperature, and a room temperature represents
22.+-.5.degree. C. (17.degree. C. to 27.degree. C.).
[0015] The steel plate according to the present invention has a
steel thickness of 40 mm or more and when the steel plate is
affected by residual stress due to welding or the like, there is
concern of delayed cracking due to hydrogen. Therefore, the carbon
equivalent Ceq (%) obtained by Equation (2) is less than 0.800%. By
causing the index Q obtained by Equation (1) to be 0.00 or more,
the hardness difference between the surface layer portion and the
thickness center portion at a room temperature becomes 15.0% or
less of the hardness at the surface layer portion, so that a steel
plate having a small hardness difference, a low carbon equivalent,
a steel thickness of 40 mm or more, and excellent, wear resistance
can be obtained. The unit of the index Q obtained by substituting
dimensionless numerical values for the steel thickness T and the
amount [X] of each element X in Equation (1) is dimensionless. In
addition, the unit of the carbon equivalent Ceq obtained by
Equation (2) is "%".
Q=0.18-1.3(logT)+0.75(2.7.times.[C]+[Mn]+0.45.times.[Ni]+0.8.times.[Cr]+-
2.times.[Mo]) (1)
Ceq(%)=[C]+[Mn]/6+[Si]/24+[Ni]/40+[Cr]/5+[Mo]/4+[V]/4 (2)
[0016] Here, the index Q of Equation (1) is calculated by
substituting the numerical value of the steel thickness T (mm), the
numerical value of the amount [X] of each element X in terms of
mass % and 0 in a case where the element X is not contained. The
carbon equivalent Ceq (%) of Equation (2) is calculated by
substituting the numerical value of the amount [X] of each element
X in terms of mass % and 0 in a case where the element X is not
contained.
[0017] The present invention has been made based on the above
findings, and the gist thereof is as follows.
[0018] [1] A steel plate according to an aspect of the present
invention includes, as a chemical composition, by mass %:
[0019] C: 0.20% to 0.35%;
[0020] Si: more than 1.00% to 2.00%;
[0021] Mn: 0.60% to 2.00%;
[0022] Cr: 0.10% to 2.00%;
[0023] Mo: 0.05% to 100%;
[0024] Al: 0.010% to 0.100%;
[0025] N: 0.0020% to 0.0100%;
[0026] B: 0.0003% to 0.0020%;
[0027] P: 0.0200% or less;
[0028] S: less than 0.0100%;
[0029] Cu: 0% to 0.500%;
[0030] Ni: 0% to 1.00%;
[0031] Nb: 0% to 0.05%;
[0032] V: 0 to 0.120%;
[0033] Ti: 0% to 0.025%;
[0034] Ca: 0% to 0.050%;
[0035] Mg: 0% to 0.050%;
[0036] REM: 0% to 0.100%; and
[0037] a remainder consisting of Fe and impurities,
[0038] in which an index Q obtained by Equation (1) is 0.00 or
more;
[0039] a carbon equivalent Ceq (%) obtained by Equation (2) is less
than 0.800%;
[0040] a ratio of a difference between a hardness at a surface
layer portion and a hardness at a thickness center portion to the
hardness at the surface layer portion at a room temperature is
15.0% or less and the hardness at the surface layer portion at a
room temperature is 400 or more in terms of Vickers hardness;
and
[0041] a steel thickness T is 40 mm or more.
Q=0.18-1.3(logT)+0.75(2.7.times.[C]+[Mn]+0.45.times.[Ni]+0.8.times.[Cr]+-
2.times.[Mo]) (1)
Ceq(%)=[C]+[Mn]/6+[Si]/24+[Ni]/40+[Cr]/5+[Mo]/4+[V]/4 (2)
[0042] where the index Q of Equation (1) is calculated by
substituting; a numerical value of the steel thickness (mm), a
numerical value of an amount [X] of each element X in terms of mass
% and 0 in a case where the element X is not contained, the carbon
equivalent Ceq (%) of Equation (2) is calculated by substituting a
numerical value of an amount [X] of each element X in terms of mass
% and 0 in a case where the element X is not contained.
[0043] [2] In the steel plate according to [1], the index Q may be
0.04 or more, and the ratio may be 13.0% or less.
[0044] [3] In the steel plate according to 1 or [2], as the
chemical composition, by mass %;
[0045] Ni is 0.05% to 1.00%.
[0046] [4] In the steel plate according to any one of [1] to [3],
as the chemical composition, by mass %,
[0047] Mn is 0.63% to 2.00%.
Effects of the Invention
[0048] According to the aspect of the present invention, it is
possible to provide a steel plate having excellent wear resistance,
in which high hardness can be maintained even in a high-temperature
environment as well as at a room temperature, the carbon equivalent
Ceq (%) of a steel plate particularly having a steel thickness of
40 mm or more is less than 0.800%, and the difference between the
hardness at the surface layer portion and the hardness at the
thickness center portion at a room temperature is set to 15.0% or
less of the hardness at the surface layer portion. The steel plate
according to the present invention can be used over a long period
of time even in a severe environment at a temperature of about
150.degree. C. to 300.degree. C. and thus the contribution thereof
to the industry is extremely remarkable.
BRIEF DESCRIPTION OF THE DRAWINGS
[0049] FIG. 1 is a view illustrating a change in the difference
between a surface hardness of a steel plate and a reference
hardness with temperature.
[0050] FIG. 2 is a view illustrating hardness distributions of
steel plates in a through-thickness direction.
[0051] FIG. 3 is a view illustrating the relationship between a
hardness difference ratio .DELTA.Hv/Hvs of the steel plate and an
index Q.
EMBODIMENTS OF THE INVENTION
[0052] The relationship between the Si content of a steel plate and
a change in hardness with temperature will be described with
reference to FIG. 1. FIG. 1 is a view illustrating a change in the
difference between a surface hardness of the steel plate and a
reference hardness with temperature. A result of performing
hardening on steel plates having a constant C content, a varying Si
content, and a steel thickness of 40 mm and measuring the Vickers
hardness (surface hardness) HV5 at the surface of the steel plate
from a room temperature to 400.degree. C. is shown in FIG. 1. The
vertical axis in FIG. 1 is the difference between the Vickers
hardness (surface hardness) HV5 at each temperature of each steel
and the Vickers hardness (reference hardness) HV5 at a room
temperature of a steel plate having a Si content of 0.25%. The
Vickers hardness HV5 was measured by cutting out a sample from a
position of 5 mm deep from the surface of the steel plate and
conducting a high-temperature Vickers hardness test based on JIS Z
2252-1991 with a test force of 49.03 N (5 kgf). The reference
hardness was measured under the same conditions as those of the
high-temperature Vickers hardness test described above except for
temperature control.
[0053] From FIG. 1, it can be seen that the room temperature
hardness and, the high-temperature hardness are increased by the
increase in the Si content and a reduction in hardness (the
difference between the surface hardness and the reference hardness)
in a high-temperature environment also decreases. As described
above, it can be seen that a steel plate containing Si in an amount
of more than 1.00% to 2.00% can secure hardness at a room
temperature and high temperatures and thus has excellent wear
resistance.
[0054] Next, FIG. 2 shows hardness distributions (Vickers hardness)
of steel plates (steel thickness 40 mm) containing Si in an amount
of more than 1.00% in the through-thickness direction after
hardening. The Vickers hardness HV5 was measured based on JIS Z
2244: 2009 at a room temperature with a test force of 49.03 N (5
kgf). As shown in FIG. 2, a hardness at a thickness center portion
is lower than a hardness at a surface layer portion. Furthermore,
from the results of the Vickers hardness test, the hardness at the
surface layer portion Hvs (the average value of Vickers hardnesses
measured in a range of 1 mm to 5 mm from the surface of the steel
plate in the through-thickness direction) and the hardness at the
thickness center portion Live (the average value of Vickers
hardnesses measured in a range of .+-.5 mm (10 mm in total
thickness) from the center portion of the steel plate in the
through-thickness direction) were obtained, and the difference
(hardness difference) .DELTA.Hv between the hardness at the
thickness center portion and the hardness at the surface layer
portion at a room temperature was calculated. That is, .DELTA.Hv is
expressed by Equation (a).
.DELTA.Hv=Hvs-Hvc (a)
[0055] The results of the Vickers hardness test are shown in Table
1. From Table 1, it can be seen that .DELTA.Hv increases with an
increase in the Si content. As described above, the inventors finds
that a thick steel plate having a large Si content tends to cause a
difference between the hardness at the surface layer portion and
the hardness at the thickness center portion at a room
temperature.
TABLE-US-00001 TABLE 1 Test steel .DELTA.Hv (HV5) 0.27% C--1.01% Si
43 0.27% C--1.51% Si 64 0.27% C--1.97% Si 79
[0056] Therefore, the inventors conducted examinations on a method
of reducing the hardness difference between the surface layer
portion and the thickness center portion at a room temperature in a
steel plate containing Si in an amount of more than 1.00% and
having a steel thickness of 40 mm or more. The inventors repeatedly
conducted examinations to reduce the hardness difference of the
steel plate in consideration of the hardenability of alloying
elements and the steel thickness.
[0057] In order to secure the hardness of the steel plate, in hot
rolling, the steel plate is typically reheated to a temperature of
the Ac.sub.3 point or higher at which transformation to austenite
ends when the temperature rises, and thereafter subjected to water
cooling or the like (hardening). At this time, the cooling rate at
the surface layer portion of the steel plate is fast and thus
sufficient hardness can be secured. On the other hand, the cooling
rate at the thickness center portion of the steel plate is lower
than that of the hardness at the surface layer portion, so that the
formation of martensite becomes insufficient, resulting in a
decrease in hardness.
[0058] As described above, the cooling rate decreases at the
thickness center portion of the steel plate. Therefore, in order to
secure a sufficient hardness at the thickness center portion of the
steel plate, it is necessary to increase the amounts of the
alloying elements to increase hardenability. However, in a case
where the amounts of the alloying elements are constant, there are
problems that the hardenability becomes insufficient depending on
the steel thickness, and the costs are increased, or weldability is
impaired by including unnecessary amounts of the alloying elements.
Therefore, in order to control the amounts of the alloying elements
within appropriate ranges, it is necessary to consider the
influence of the steel thickness on the cooling rate at the
thickness center portion.
[0059] The inventors establishes the relationship between the
amounts of the alloying elements having hardenability and the steel
thickness, which influences the hardness difference ratio
.DELTA.Hv/Hvs of various steels containing Si in an amount of more
than 1.00% and having a steel thickness of 40 mm or more, and
derives an index Q shown in Equation (1). The hardness difference
ratio .DELTA.Hv/Hvs (%) represents the ratio obtained by dividing
the difference between the hardness at the surface layer portion
and the hardness at the thickness center portion at a room
temperature by the hardness at the surface portion as a percentage.
In addition, the hardness difference ratio .DELTA.Hv/Hvs (%) is
expressed by Equation (b). In Equation (b), Hvs is the hardness at
the surface layer portion (the average value of Vickers hardnesses
measured in a range of 1 mm to 5 mm from the surface of the steel
plate in the through-thickness direction), and the live is the
hardness at the thickness center portion (the average value of
Vickers hardnesses measured in a range of .+-.5 mm (10 mm in total
thickness) from the center portion of the steel plate in the
through-thickness direction).
.DELTA.Hv/Hvs(%)=100.times.(Hvs-Hvc)/Hvs (b)
[0060] In the related art, it has been thought that the
hardenability of a steel containing Si in an amount of more than
1.00% decreases as the cooling rate decreases. However, the
inventors finds that when hardenability is secured by including
alloying elements (C, Mn, Ni, Cr, and Mo) in addition to Si in the
steel containing Si in an amount of more an 1.00%, Si contributes
to the improvement in hardenability even when the cooling rate
decreases. Equation (1) is based on the finding of the inventors
that it is necessary to secure hardenability by including the
alloying elements (C, Mn, Ni, Cr, and Mo) in addition to Si in
order to increase the hardness at the thickness center portion, and
the index Q does not include a Si content term.
Q=0.18-1.3(logT)+0.75(2.7.times.[C]+[Mn]+0.45.times.[Ni]+0.8.times.[Cr]+-
2.times.[Mo]) (1)
[0061] Here, the index Q of Equation (1) is calculated by
substituting the numerical value of the steel thickness T (mm), the
numerical value of the amount [X] of each element X in terms of
mass % and 0 in a case where the element X is not contained. The
index Q is calculated by substituting dimensionless numerical
values for the steel thickness T and the amount [X] of each element
in Equation (1). In addition, log in Equation (1) is the logarithm
to base 10, that is, the common logarithm.
[0062] FIG. 3 shows the relationship between the hardness
difference ratio .DELTA.Hv/Hvs (%) and the index Q. From FIG. 3, it
is found that in a case where the hardness difference ratio
.DELTA.Hv/Hvs (%) is set to 15.0% or less of the hardness at the
surface layer portion Hvs as a criterion for causing a thick steel
plate to have a long service life, it is necessary to satisfy
Q.gtoreq.0.00. In addition, it is found that in a case of setting
the hardness difference ratio .DELTA.Hv/Hvs (%) to 13.0% or less of
the hardness at the surface layer portion Hvs, it is necessary to
satisfy Q.gtoreq.0.04.
[0063] Furthermore, since the steel plate according to this
embodiment has a steel thickness of 40 mm or more, there is concern
of hydrogen embrittlement cracking under the influence of residual
stress due to welding. Therefore, the carbon equivalent Ceq (%)
expressed by Equation (2) is less than 0.800%. Equation (2)
includes a Si content term because, the weldability of the steel
plate needs to be taken into consideration.
Ceq(%)=[C]+[Mn]/6+[Si]/24+[Ni]/40+[Cr]/5+[Mo]/4+[V]/4 (2)
[0064] The carbon equivalent Ceq (%) of Equation (2) is calculated
by substituting the numerical value of the amount [X] of each
element X in terms of mass %, and 0 is substituted in a case where
the element X is not contained. The unit of the carbon equivalent
Ceq obtained by Equation (2) is "%".
[0065] By causing the index Q in Equation (1) to be 0.00 or more,
the hardness difference .DELTA.Hv between the surface layer portion
and the thickness center portion of the steel plate at a room
temperature becomes 15.0% or less of the hardness at the surface
layer portion Hvs, so that a steel plate having a small hardness
difference, a carbon equivalent of less than 0.800%, a steel
thickness of 40 mm or more, and excellent wear resistance can be
obtained.
[0066] Hereinafter, the steel plate according to this embodiment
will be described in detail. First, the chemical composition of the
steel plate according to this embodiment will be described, Unless
otherwise specified, % regarding the chemical composition means
mass %.
[0067] <C: 0.20% to 0.35%>
[0068] C is an element effective for improving the hardness, and
the C content is set to 0.20% or more in order to secure the
hardness of the steel plate. The C content is preferably 0.22% or
more, and more preferably 0.24% or more. On the other hand, when
the C content exceeds 0.35%, the susceptibility to hydrogen
embrittlement increases due to are increase in hardness, and there
is concern of the occurrence of cracking due to hydrogen
embrittlement. Therefore, the C content is set to 0.35% or less.
The C content is set to preferably 0.32% or less, and more
preferably 0.30% or less.
[0069] <Si; More Than 1.00% to 2.00%>
[0070] Si is a deoxidizing agent and is an element effective for
improving the hardness of the steel plate. In this embodiment, Si
is an extremely important element for maintaining the hardness of
the steel plate in a high-temperature environment. In order to
obtain the effect of containing Si, the Si content is set to be
more than 1.00%, The Si content is preferably 1.10% or more, and
more preferably 1.20% or more, or 1.30% or more. On the other hand,
when the Si content exceeds 2.00%, the toughness of the steel plate
may be impaired, so that the Si content is set to 2.00% or less.
The Si content is set to preferably 1.90% or less, and more
preferably 1.80% or less.
[0071] <Mn: 0.60% to 2.00%>
[0072] Mn is an element which increases the hardenability and
improves the hardness, and needs to be contained, in an amount of
0.60% or more in order to secure the hardness of the steel plate.
The Mn content is preferably 0.70% or more, and more preferably
0.80% or more. On the other hand, excessive inclusion of Mn lowers
the toughness and accelerates the formation of cementite, resulting
in a decrease in the high-temperature hardness of the steel plate.
Therefore, the Mn content is set to 2.00% or less. The Mn content
is set to preferably 1.50% or less or 1.35% or less, and more
preferably 1.20% or less or 1.00% or less.
[0073] <Cr: 0.10% to 2.00%>
[0074] Cr is an element which increases the hardenability and
improves the toughness and hardness of the steel plate. In order to
secure the toughness and hardness of the steel plate, the Cr
content is set to 0.10% or more. The Cr content is preferably 0.50%
or more, and more preferably 0.80% or more. On the other hand, when
the Cr content exceeds 2.00%, the toughness of the steel plate
decreases, so that the Cr content is set to 2.00% or less. The Cr
content is set to preferably 1.70% or less, and more preferably
1.50% or less.
[0075] <Mo: 0.05% to 1.00%>
[0076] Mo is also an element which increases the hardenability and
improves the hardness of the steel plate. In addition, Mo is an
element effective for maintaining the hardness of the steel plate
even in a high-temperature environment. Therefore, the Mo content
is set to 0.05% or more. The Mo content is set to preferably 0.10%
or more, and more preferably 0.20% or more. On the other hand, when
the Mo content exceeds 1.00%, the toughness of the steel plate
decreases, so that the Mo content is set to 1.00% or less. The Mo
content is set to preferably 0.60% or less, and more preferably
0.40% or less.
[0077] <A1: 0.010% to 0.1.00%>
[0078] A1 is an element effective as a deoxidizing agent. In
addition, A1 is bonded to N to form in AlN, and refines crystal
grains, thereby improving the toughness of the steel plate.
Therefore, the Al content is set to 0.010% or more. The Al content
is set to preferably 0.020% or more, and more preferably 0.030% or
more. On the other hand, when Al is excessively contained, the
toughness of the steel plate decreases, so that the Al content is
set to 0.100% or less. The Al content is set to preferably 0.080%
or less, and more preferably 0.070% or less.
[0079] <N: 0.0020% to 0.0100%>
[0080] N is an element that is bonded to Al and Ti to form
nitrides, and refines crystal grains, thereby improving the
toughness of the steel plate. Therefore, the N content is set to
0.0020% or more. The N content is set to preferably 0.0030% or
more, and more preferably 0.0040% or more. On the other hand, when
N is excessively contained, coarse nitrides are formed and the
toughness of the steel plate decreases, so the N content is set to
0.0100% or less. The N content is set to preferably 0.0080% or
less, and more preferably 0.0060% or less.
[0081] <B: 0.0003% to 0.0020%>
[0082] B is, an element that significantly increases the
hardenability of steel and is particularly effective for improving
the hardness at the thickness center portion of the steel plate.
Therefore, the B content is set to 0.0003% or more. The B content
is set to preferably 0.0005% or more, more preferably 0.0007% or
more, and even more preferably 0.0010% or more. On the other hand,
in a case where B is excessively contained, boride is formed, the
hardenability decreases, and the hardness of the steel plate cannot
be secured. Therefore, the B content is set to 0.0020% or less. The
B content is preferably 0.0018% or less, and more preferably
0.0016% or less.
[0083] <P: 0.0200% or Less>
[0084] P is an impurity, and reduces, the toughness and workability
of the steel plate. Therefore, the P content is limited to 0.0200%
or less. The P content is set to preferably 0.0150% or less, and
more preferably 0.0100% or less. The lower limit of the P content
is preferably 0%, but from the viewpoint of manufacturing costs,
the P content may be 0.0001% or more
[0085] <S: Less Than 0.0100%>
[0086] Like P, S is an impurity and reduces the toughness of the
steel plate. Therefore, the S content is limited to less than
0.0100%. The S content is set to preferably 0.0070% or less, more
preferably 0.0050% or less, and even more preferably 0.0030% or
less. The lower limit of the S content is preferably 0%, but from
the viewpoint of manufacturing costs, the S content may be 0.0001%
or more.
[0087] In the steel plate according to this embodiment, one or more
of Cu, Ni, Nb, V, and Ti can be selectively contained for, the
purpose of improving the mechanical properties such as the hardness
and toughness of the steel plate. The lower limit of the amounts of
these elements is 0%.
[0088] <Cu: 0% to 0.50%>
[0089] Cu is an element that forms fine precipitates and
contributes to the improvement of the strength (4 the steel plate,
and may be contained in an amount of 0.001% or more. The Cu content
is set to more preferably 0.050% or more, and even more preferably
0.100% or more. On the other hand, when Cu is excessively
contained, the wear resistance of the steel plate is deteriorated,
so that the upper limit of the Cu content is set to 0.500% or less.
The Cu content is set to more preferably 0.450% or less, and even
more preferably 0.400 or less.
[0090] <Ni: 0% to 1.00%>
[0091] Ni is an element that increases the hardenability of the
steel and contributes to the in of the hardness of the steel plate,
and may be contained in an amount of 0.05% or more. The Ni content
is set to more preferably or more, and even more preferably 0.20%
or more. On the other hand, since Ni is an expensive alloying
element, from the viewpoint of costs, the Ni content is set to
1.00% or less. The Ni content is set to more preferably 0.70% or
less, and even more preferably 0.50% or less.
[0092] <Nb: 0% to 0.050%>
[0093] Nb is an element contributing to grain refinement by the
formation of nitride and suppressing recrystallization, and may be
contained in an amount of 0.005% or more in order to improve the
toughness of the steel plate. The Nb content is set to more
preferably 0.007% or more, and even more preferably 0.010% or more.
On the other hand, when Nb is excessively contained, the toughness
of the steel plate may decrease. Therefore, the Nb content is set
to 0.050% or less. The Nb content is set to more preferably 0.030%
or less, and even more preferably 0.020% or less.
[0094] <V: 0% to 0.120%>
[0095] V is an element that contributes to the improvement of the
hardness of the steel plate, and may be contained in an amount of
0.010% or more. The V content is set to more preferably 0.020% or
more, and even more preferably 0.040% or more. On the other hand,
when V is excessively contained, there may be cases where cracking
occurs in cast pieces and the manufacturability may be impaired.
Therefore, the V content is set to 0.120% or less. The V content is
set to more preferably 0.100% or less, and even more preferably
0.070% or less.
[0096] <Ti: 0% to 0,025%>
[0097] Ti is an element that forms TiN, refines crystal grains, and
thus improves the toughness of the steel plate, and may be
contained in an amount of 0.005% or more. The Ti content is set to
more preferably 0.007% or more, and even more preferably 0.010% or
more. On the other hand, excessive inclusion of Ti may reduce the
toughness of the steel plate, so that the Ti content is set to
0.025% or less. The Ti content is set to more preferably 0.020% or
less, and even more preferably to 0.015% or less.
[0098] In order to control the morphology and the like of the
inclusions in the steel, one or more of Ca, Mg, and REM can be
selectively contained. The lower limit of the amounts of these
elements is 0%.
[0099] <Ca: 0% to 0.050%>
[0100] <Mg: 0% to 0.050%>
[0101] <REM: 0% to 0.100%>
[0102] Any of Ca, Mg, and REM is an element that is bonded to S to
form sulfides and forms inclusions that are less likely to be
stretched by hot rolling, and mainly contributes to the improvement
of the toughness of the steel plate. On the other hand, when Ca,
Mg, and REM are excessively contained, these elements form coarse
oxides with O, and there may be cases where the toughness of the
steel plate may decrease. Therefore, each of the Ca content and the
Mg content is set to 0.050% or less, and the REM content is set to
0.100% or less. Each of the Ca content, the Mg content, and the REM
content is each set to more preferably 0.020% or less, and even
more preferably 0.010% or less, or 0.005% or less. On the other
hand, in order to obtain the effect of improving the toughness of
the steel plate, it is preferable that each of the Ca content and
the Mg content is set to 0.0005% or more, and the REM content is
set to 0.001% or more. More preferably, each of the Ca content and
the Mg content is set to 0.0007% or more, and the REM content is
set to 0.002% or more.
[0103] REM (rare-earth metal elements) means a total of 17 elements
including Sc, Y, and lanthanoid. The REM content means the total
amount of these 17 elements.
[0104] The remainder of the chemical composition of the steel plate
according to this embodiment consists of Fe and impurities. Here,
the impurities mean elements that are incorporated when a steel
plate is industrially manufactured, due to various factors in a
manufacturing process including raw materials such as ore and
scrap, and are acceptable within a range in which the
characteristics of the steel plate according to this embodiment are
not adversely affected. However, in the steel plate according to
this embodiment, the upper limits of P and S among the impurities
need to be specified as described above.
[0105] Furthermore, there may be cases where one or more of O, Sb,
Sn, and As may be incorporated as impurities in the steel. Even if
these impurities are incorporated, there is no particular problem
as long as these impurities are in a typical incorporation level
(content range) of wear-resistant steel. Therefore, the amounts
thereof are limited to the typical incorporation level of the
wear-resistant steel as described below. The lower limit of the
amounts of these impurities is 0%.
[0106] <O: 0.006% or Less>
[0107] O may be incorporated as an impurity in the steel, in some
cases. However, since O is an element that forms coarse oxides, the
O content is preferably small. In particular, when the O content
exceeds 0.006%, coarse oxides arc formed in the steel and the wear
resistance of the steel plate deteriorates. Therefore, the O
content is set to 0.006% or less. The O content is set to
preferably 0.005% or less, and more preferably to 0.004% or
less.
[0108] <Sb: 0.01% or Less>
[0109] Sb is an element incorporated from scrap as a steel raw
material. In particular, when Sb is excessively contained, the wear
resistance of the steel plate deteriorates, so that the Sb content
is set to 0.01% or less. The Sb content is set to preferably 0.007%
or less, or 0.005% or less.
[0110] <Sn: 0.01% or Less>
[0111] Like Sb, Sn is an element incorporated from scrap as a steel
raw material. In particular, when Sn is excessively contained, the
wear resistance of the steel plate deteriorates, so that the Sn
content is set to 0.01% or less. The Sn content is set to
preferably 0.007% or less, or 0.005% or less.
[0112] <As: 0.01% or Less>
[0113] Like Sb and Sn, As is an element incorporated from scrap as
a steel raw material. In particular, when As is excessively
contained, the wear resistance of the steel plate deteriorates, so
that the As content is set to 0.01% or less. The As content is set
to preferably 0.007% or less, or 0.005% or less.
[0114] In the steel plate according to this embodiment, the index Q
obtained by Equation (1) is set to 0.00 or more so that the
hardness difference between the surface layer portion and the
thickness center portion of the steel plate at a room temperature
is small and the ratio of the hardness difference to the hardness
at the surface layer portion is 15.0% or less. The index Q is
calculated by substituting dimensionless numerical values for the
numerical value of the steel thickness T (mm) and the numerical
value of the amount [X] of each element X in terms of mass %, and
[X] is set to 0 in a case where the element X is not contained. In
order to reduce the hardness difference between the surface layer
portion and the thickness center portion of the steel plate, the
index Q is set to preferably 0.01 or more, more preferably 0.04 or
more, even more preferably 0.05 or more, and still more preferably
0.10 or more. The upper limit of the index Q is not particularly
specified. However, since the carbon equivalent Ceq (%) also
increases as the index Q increases, the index Q is limited by
itself. In order to secure the weldability by causing the carbon
equivalent Ceq (%) to be less than 0.800%, the index Q is
preferably 1.10 or less. The index Q is set to more preferably 0.80
or less or 0.50 or less, and more preferably 0.30 or less or 0.20
or less.
Q=0.18-1.3(logT)+0.75(2.7).times.[C]+[Mn]+0.45.times.[N]+0.8.times.[Cr]+-
2.times.[Mo]) (1)
[0115] In the steel plate according to this embodiment, in order to
suppress weld cracking and secure the weldability of the steel
plate, the carbon equivalent Ceq (%) is set to be less than 0.800%.
The carbon equivalent Ceq (%) is calculated by substituting the
numerical value of the amount [X] of each element in terms of mass
%, and [X] is set to 0 in a case where the element X is not
contained. The lower limit of the carbon equivalent is not
particularly specified. However, since the index Q also increases
as the carbon equivalent Ceq (%) decreases, the carbon equivalent
Ceq (%) is limited by itself. In order to reduce the hardness
difference by setting the index Q to 0.00 or more, the carbon
equivalent Ceq (%) is preferably 0.507% or more. In order to
increase the ear resistance of the steel plate, the carbon
equivalent Ceq (%) is set to more preferably 0.600% or more, and
more preferably 0.650% or more. The carbon equivalent Ceq (%) is
set to even more preferably 0.700% or more. In order to enhance the
weldability of the steel plate, the carbon, equivalent Ceq (%) may
be 0.785% or less, 0.770% or less, or 0.760% or less.
Ceq(%)=[C]+[Mn]/6+[Si]/24+[Ni]/40+[Cr]/5+[Mo]/4+[V]/4 (2)
[0116] In the steel plate according to this embodiment, since the
difference (hardness difference) between the hardness at the
surface layer portion and the hardness at the thickness center
portion at a room temperature is small and the ratio of the
difference between the hardness at the surface layer portion and
the hardness at the thickness center portion to the hardness at the
surface layer portion is 15.0% or less, excellent wear resistance
can be exhibited over a long period of time. It is preferable that
the hardness difference ratio .DELTA.Hv/Hvs) is as small as
possible. However, it is difficult to set the hardness difference
ratio .DELTA.Hv/Hvs (%) to be less than 0% or less than 1.0%.
Therefore, the lower limit thereof may be set to 0% or 1.0%. In
consideration of an increase in costs due to an increase in the
amounts of the alloying elements, the hardness difference ratio
.DELTA.Hv/Hvs (%) may be 3.0% or more. The hardness at the surface
layer portion and the hardness at the thickness center portion are
Vickers hardnesses HV5 at a room temperature and are measured based
on JIS Z 2244:2009. The hardness at the surface layer portion is
measured using a section parallel to the rolling direction and the
through-thickness direction of the steel plate as a measurement
surface, and is the average value of Vickers hardnesses HV5
measured in a range of 1 mm to 5 mm from the surface of the steel
plate in the through-thickness direction. In the measurement of the
hardness at the surface layer portion and the steel plate, Vickers
hardnesses at a total of 25 points, 5 points at least every 1 mm in
the range are measured. The hardness at the thickness center
portion is the average value of Vickers hardnesses HV5 measured in
a range of .+-.5 mm (10 mm in total thickness) from the thickness
center portion of the steel plate in the through-thickness
direction on the measurement surface. In the measurement of the
hardness at the thickness center portion of the steel plate,
Vickers hardnesses at a total of 55 points, 5 points at least every
1 mm in the range are measured.
[0117] In the steel plate according to this embodiment, the
hardness at the surface layer portion Hvs at room temperature is
400 or more in terms of Vickers hardness (HV5). When the hardness
at the surface layer portion Hvs is less than 400 in terms of
Vickers hardness (HV5), the strength of the hardness at the surface
layer portion of the steel plate is insufficient, and cannot be
used for applications such as construction machines and industrial
machines. In order to improve the wear resistance, the hardness at
the surface layer portion Hvs at room temperature may be 440 or
more, 460 or more, 480 or more, or 500 or more in terms of Vickers
hardness (Hv5).
[0118] The steel plate according to this embodiment exhibit very
high hardness from the hardness at the surface layer portion to the
hardness at the thickness center portion and very high tensile
strength. As necessary, the tensile strength (TS) thereof at room
temperature may be set to 1000 MPa or more, 1200 MPa or more, 1350
MPa or more, or 1500 MPa or more. The upper limit of the tensile
strength does not need to be particularly determined, but may be
2300 MPa or less. The tensile strength is measured based on JIS Z
2241;2011 by extracting an overall thickness test piece (that is, a
plate-shaped test piece) or a round bar test piece from a position
(T/4) away from the surface of the steel plate by 1/4 of the steel
thickness T.
[0119] The steel plate according to this embodiment is a steel
plate manufactured by hot rolling and is a steel plate having a
steel thickness of 40 mm or more, preferably 42 mm or more or 50 mm
or more, and more preferably 60 mm or more or 80 mm or more. The
upper limit of the steel thickness is not particularly specified,
and may be 150 mm depending on the application. In consideration
homogenization of the properties of the steel plate in the
through-thickness direction, the steel thickness may be set to 100
mm or less.
[0120] A method of manufacturing the steel, plate according to this
embodiment will be described. In this embodiment, the steel piece
having the above-described chemical composition can be manufactured
by a known method such as a continuous casting method of an
ingot-making and blooming method after melting in a typical
refining process using a converter, an electric furnace, or the
like, and there is no particular limitation.
[0121] In this embodiment, the steel piece obtained by casting is
hot-rolled, water-cooled as it is or air-cooled, and thereafter
reheated and hardened, thereby manufacturing the steel plate.
However, the steel plate is hardened but is not subjected to a heat
treatment such as tempering.
[0122] A steel may be subjected to melting, casting, and thereafter
hot rolling as it is. However, a steel piece may be once cooled to
room temperature, reheated to a temperature of the Ac.sub.3 point
or higher, and then hot rolled. The Ac.sub.3 point is a temperature
at which the structure of the steel becomes austenite (austenitic
transformation is completed) due to a temperature rise. The heating
temperature of the hot rolling is set to preferably 900.degree. C.
or higher, and more preferably 1000.degree. C. or higher in order
to reduce the deformation resistance. On the other hand, when the
heating temperature of the hot rolling is too high, the structure
becomes coarse and the low-temperature toughness of the steel plate
sometimes decreases. Therefore, the heating temperature is
preferably 1250.degree. C. or lower. The heating temperature is
more preferably 1200.degree. C. or lower, and even more preferably
1150.degree. C. or lower.
[0123] It is preferable that the hot rolling is ended at the
Ar.sub.3 point or higher, which is the temperature at which
ferritic transformation starts by a temperature decrease. The
Ac.sub.3 point and the Ar.sub.3 point can be obtained by extracting
a test piece from a steel piece and obtaining a thermal expansion
behavior at the time of heating and cooling. The steel plate is
hardened to a temperature of 250.degree. C. or lower immediately
after the hot rolling, or is air-cooled after the hot rolling,
reheated to a temperature of the Ac.sub.3 point or higher, hardened
to a temperature of 250.degree. C. or lower.
EXAMPLES
[0124] Hereinafter, the present invention will be described in more
detail by employing examples of the steel plate according to the
present invention. However, the present invention is not limited to
the following examples as a matter of course, and can be embodied
by appropriately adding changes within a range that is appropriate
for the gist of the present invention, and all such changes are
included in the technical scope of the present invention.
[0125] A steel having a chemical composition shown in Table 2 was
melted, cast, thereafter hot-rolled into a steel plate having a
steel thickness shown in Table 3, and air-cooled to room
temperature. Thereafter, a steel plate having a steel thickness of
40 mm or more was manufactured by increasing the temperature to a
hardening temperature shown in Table 3 and performing hardening
thereon. A test piece was extracted from the obtained steel plate,
and using a section of the steel plate parallel to the rolling
direction and the through-thickness direction as a test surface,
the Vickers hardnesses at the surface layer portion and the
thickness center portion were measured based on JIS Z 2244:2009 at
room temperature with a test force of 49.03 N (5 kgf). The Vickers
hardness (a hardness at the surface layer portion) Hvs of at the
surface layer portion was obtained by measuring Vickers hardnesses
at a total of 25 points, 5 points every 1 mm, in a range (surface
layer portion) of 1 mm to 5 mm from the surface of the steel plate
in the through-thickness direction, and obtaining the average value
(arithmetic mean) thereof. The Vickers hardness (hardness at a
thickness center portion) Hvc of the thickness center portion was
obtained by measuring Vickers hardnesses at a total of 55 points, 5
points every 1 mm, in a range of .+-.5 mm (10 mm in total
thickness) from the thickness center portion of the steel plate in
the through-thickness direction, and obtaining the average value
(arithmetic mean) thereof. Using the values of the hardness at the
surface layer portion Hvs and the hardness at the thickness center
portion Hvc obtained as described above, the hardness difference
ratio .DELTA.Hv/Hvs (%) representing the hardness difference
between the surface layer portion and the thickness center portion
of the steel plate at a room temperature was obtained. The hardness
difference ratio .DELTA.Hv/Hvs (%) is expressed by Equation
(b).
.DELTA.Hv/Hvs(%)=100.times.(Hvs-Hvc)/Hvs (b)
[0126] In addition, a sample was cut out from the steel plate, and
a high-temperature Vickers hardness test was conducted thereon
based on JIS Z 2252-1991 at 400.degree. C. with a test force of
9.807 N (1 kgf). Accordingly, the high-temperature hardness (HV1)
at the surface layer portion of the steel plate was obtained. The
measurement of the high-temperature hardness at the surface layer
portion was performed under the same condition as the surface layer
portion Vickers hardness test (room temperature) except for the
temperature control and test force. Furthermore, a full-size V
notch Charpy test piece in a direction parallel to the rolling
direction was cut out from a position (T/4) away from the surface
of the steel plate by 1/4 of the steel thickness T, and a Charpy
absorbed energy (vE.sub.0) at 0.degree. C. was measured based on
JIS 2242:2005.
[0127] The criteria of evaluation items are as follows. Regarding
both the hardness at the surface layer portion Hvs (HV5) and the
hardness at the thickness center portion Hvc (HV5), a hardness of
400 or more was determined to be good from the viewpoint of wear
resistance, and a hardness of 600 or less was determined to be good
from the viewpoint of cutting workability. Regarding the
high-temperature hardness (HV5) at the surface layer portion, a
hardness of 300 or more was determined to be good from the
viewpoint of wear resistance at high temperatures. A Charpy
absorbed energy at 0.degree. C. of 15 J or more was determined to
be good.
[0128] The results are shown in Table 3. In Nos. 1 to 18, the
parameters of the chemical composition including the index Q and
the carbon equivalent Ceq (%) and the steel thickness T are within
the ranges of the present invention, and the hardness difference
ratio .DELTA.Hv/Hvs between the surface layer portion and the
center portion is 15.0% or less. Any of these steels is a steel
plate excellent in the hardness at the surface layer portion Hvs,
the hardness at the thickness center portion live, the
high-temperature hardness at the surface layer portion, and the
Charpy absorbed energy at 0.degree. C.
TABLE-US-00002 TABLE 2 Steel Chemical composition (mass %)
remainder consisting of Fe and impurities No. C Si Mn Cr Mo Al N B
P S A1 0.27 1.02 0.90 0.99 0.25 0.042 0.0052 0.0011 0.0075 0.0019
A2 0.28 1.49 0.80 0.99 0.24 0.042 0.0040 0.0011 0.0075 0.0019 A3
0.27 1.93 1.05 0.99 0.20 0.062 0.0047 0.0011 0.0075 0.0019 A4 0.31
1.05 0.61 1.17 0.24 0.035 0.0045 0.0014 0.0055 0.0042 A5 0.32 1.52
0.63 1.23 0.15 0.042 0.0051 0.0013 0.0051 0.0061 A6 0.22 1.15 0.62
1.50 0.45 0.068 0.0055 0.0013 0.0085 0.0028 A7 0.22 1.10 0.90 0.65
0.35 0.042 0.0039 0.0011 0.0080 0.0010 A8 0.28 1.11 0.92 1.10 0.18
0.066 0.0042 0.0012 0.0071 0.0025 A9 0.25 1.06 0.66 1.06 0.65 0.044
0.0045 0.0011 0.0061 0.0021 A10 0.23 1.08 1.56 1.18 0.06 0.063
0.0056 0.0012 0.0053 0.0012 A11 0.34 1.60 0.65 1.25 0.08 0.076
0.0047 0.0015 0.0080 0.0064 A12 0.25 1.05 0.89 1.30 0.07 0.065
0.0052 0.0015 0.0061 0.0044 A13 0.28 1.09 0.71 1.40 0.25 0.071
0.0059 0.0015 0.0057 0.0057 A14 0.29 1.18 0.81 1.21 0.08 0.043
0.0050 0.0011 0.0069 0.0026 A15 0.23 1.31 0.92 1.10 0.18 0.040
0.0043 0.0012 0.0072 0.0021 A16 0.24 1.61 1.12 1.05 0.22 0.041
0.0044 0.0011 0.0056 0.0014 A17 0.26 1.16 0.72 1.29 0.18 0.048
0.0042 0.0012 0.0073 0.0044 A18 0.25 1.03 0.64 1.56 0.23 0.064
0.0038 0.0016 0.0077 0.0021 B1 0.18 1.40 1.50 0.80 0.05 0.035
0.0049 0.0008 0.0055 0.0023 B2 0.37 1.80 1.20 0.50 0.10 0.028
0.0055 0.0014 0.0051 0.0031 B3 0.24 0.90 1.45 1.10 0.05 0.034
0.0050 0.0007 0.0080 0.0021 B4 0.24 2.10 1.45 0.80 0.06 0.037
0.0047 0.0016 0.0077 0.0046 B5 0.27 1.42 0.45 1.48 0.06 0.044
0.0072 0.0008 0.0091 0.0029 B6 0.27 1.52 2.11 0.30 0.05 0.039
0.0068 0.0008 0.0082 0.0041 B7 0.23 1.12 1.92 0.80 0.06 0.046
0.0047 0.0015 0.0083 0.0047 B8 0.21 1.14 0.61 2.07 0.06 0.038
0.0052 0.0016 0.0057 0.0061 B9 0.24 1.06 0.81 1.55 0.04 0.043
0.0049 0.0018 0.0051 0.0028 B10 0.26 1.62 0.62 0.40 1.10 0.046
0.0051 0.0014 0.0087 0.0041 B11 0.23 1.12 1.78 0.22 0.09 0.028
0.0041 0.0002 0.0076 0.0047 B12 0.23 1.24 1.75 0.21 0.11 0.024
0.0038 0.0030 0.0096 0.0038 Chemical composition (mass %) Steel
remainder consisting of Fe and impurities Ceq No. Cu Ni Nb V Ti Ca
Mg REM (%) Remarks A1 0.015 0.101 0.019 0.748 Example A2 0.012
0.091 0.012 0.756 A3 0.773 A4 0.014 0.015 0.749 A5 0.016 0.020
0.020 0.777 A6 0.018 0.040 0.794 A7 0.40 0.020 0.012 0.643 A8 0.07
0.746 A9 0.013 0.013 0.779 A10 0.06 0.017 0.002 0.788 A11 0.050
0.002 0.798 A12 0.32 0.001 0.728 A13 0.007 0.786 A14 0.013 0.030
0.020 0.744 A15 0.016 0.085 0.014 0.724 A16 0.016 0.017 0.759 A17
0.07 0.014 0.733 A18 0.420 0.35 0.017 0.040 0.788 B1 0.014 0.012
0.661 Comparative B2 0.016 0.022 0.770 Example B3 0.012 0.752 B4
0.012 0.744 B5 0.46 0.011 0.022 0.727 B6 0.011 0.022 0.758 B7 0.011
0.628 B8 0.45 0.022 0.021 0.799 B9 0.016 0.012 0.739 B10 0.011
0.014 0.786 B11 0.017 0.017 0.640 B12 0.014 0.012 0.643 Blank means
that the element is not intentionally contained. Underlined means
out of the range of the present invention.
TABLE-US-00003 TABLE 3 High- temperature Hardening Steel
(400.degree. C.) Steel temperature thickness Hvs Hvc .DELTA.Hv/Hvs
hardness vEs No. No. (.degree. C.) (mm) Q (HV5) (HV5) (%) (HV5) (J)
Remarks 1 A1 910 50 0.16 518 483 6.8 332 30 Example 2 A2 930 42
0.19 541 486 10.2 376 26 3 A3 950 70 0.01 555 477 14.1 405 22 4 A4
910 50 0.12 544 518 4.8 340 22 5 A5 930 50 0.05 571 522 8.6 381 20
6 A6 910 102 0.05 469 445 5.1 312 47 7 A7 910 50 0.14 465 433 6.9
315 45 8 A8 910 60 0.08 526 458 12.9 357 33 9 A9 910 122 0.08 495
434 12.3 325 41 10 A10 910 80 0.14 478 437 8.6 310 22 11 A11 930 42
0.12 591 538 9.0 455 28 12 A12 910 42 0.24 492 476 3.3 359 48 13
A13 910 70 0.10 536 497 7.3 372 46 14 A14 910 42 0.11 538 493 8.4
375 30 15 A15 930 50 0.06 487 435 10.7 329 27 16 A16 950 55 0.20
515 449 12.8 385 23 17 A17 910 48 0.13 507 459 9.5 343 28 18 A18
910 85 0.06 491 447 9.0 315 26 101 A1 910 80 -0.10 505 415 17.8 324
32 Comparative 102 A5 930 80 -0.21 545 441 19.1 372 21 Example 103
A9 910 70 -0.05 481 407 15.4 345 38 104 B1 930 42 0.11 392 338 13.8
255 41 105 B2 950 42 0.17 621 580 6.6 465 23 106 B3 910 55 0.23 498
486 2.4 284 38 107 B4 950 55 0.06 531 468 11.9 402 13 108 B5 930 42
0.09 389 338 13.1 275 36 109 B6 930 42 0.45 531 525 1.1 365 14 110
B7 910 42 0.11 387 347 10.3 293 9 111 B8 910 50 0.34 472 466 1.3
308 12 112 B9 910 50 0.05 416 355 14.7 298 14 113 B10 910 50 0.85
520 505 2.9 371 12 114 B11 910 42 0.14 325 301 7.4 243 34 115 B12
910 42 0.14 356 315 11.5 254 33 Underlined means out of the range
of the present invention or out of the range of preferable
properties.
[0129] On the other hand Nos. 101 to 115 in Table 3 are comparative
examples, and the chemical compositions including the Q value are
out of the ranges of the present in Nos. 101 to 103 are examples in
which the Q value was low in relation to the steel thickness and
the hardness difference ratio .DELTA.Hv/Hvs (%) exceeded 15.0%. No.
107 is an example in which the Si content was insufficient and the
high-temperature hardness at the surface layer portion had
decreased. On the other hand, No. 107 is an example in which the Si
content was large and the toughness had decreased.
[0130] Nos. 104, 108 and 114 are examples in which the C content,
the Mn content, and the B content were insufficient, respectively,
and the hardness at the surface layer portion Hvs, the hardness at
the thickness center portion Hvc, and the high-temperature hardness
at the surface layer portion had decreased.
[0131] No. 110 in which the Cr content was insufficient is an
example in which the toughness had decreased in addition to the
hardness at the surface layer portion Hvs, the hardness at the
thickness center portion Hvc, and the high-temperature hardness at
the surface layer portion.
[0132] No. 112 in which the Mo content was insufficient is an
example in which the hardness at the thickness center portion Hvc,
the high-temperature hardness at the surface layer portion, and the
toughness had decreased.
[0133] No. 105 is an example in which the C content was large and
the hardness at the surface layer portion Hvs was excessively
high.
[0134] No. 109 with a high Mn content, No. 111 with a high Cr
content, and No. 113 with a high Mo content are examples in which
the toughness had decreased.
[0135] No. 115 with an excessive B content is an example in which
the hardness at the surface layer portion Hvs, the hardness at the
thickness center portion Hvc, and the high-temperature hardness at
the surface layer portion had decreased.
[0136] In all the examples, the O content was 0.006% or less, and
all the Sb content, the Sn content, and the As content were 0.01%
or less.
[0137] As described above, in Comparative Examples Nos. 101 to 115
in which any one or more of the chemical composition and the Q
value were out of the ranges of the present invention, at least one
of the hardness difference ratio .DELTA.Hv/Hvs, the hardness at the
surface layer portion Hvs, the hardness at a thickness center
portion Hvc, the high-temperature hardness at the surface layer
portion, and the toughness did not reach the evaluation criteria
determined to be good.
* * * * *