U.S. patent application number 11/444460 was filed with the patent office on 2006-12-21 for steel for a plastic molding die.
This patent application is currently assigned to DAIDO STEEL CO., LTD.. Invention is credited to Shuji Hamano, Motohiro Ibuki, Takeshi Koga.
Application Number | 20060285992 11/444460 |
Document ID | / |
Family ID | 36636190 |
Filed Date | 2006-12-21 |
United States Patent
Application |
20060285992 |
Kind Code |
A1 |
Ibuki; Motohiro ; et
al. |
December 21, 2006 |
Steel for a plastic molding die
Abstract
To provide a steel for plastic molding die which possesses
enough hardness, wear resistance and corrosion resistance, and is
excellent in high-precision processability and mirror polishing
properties. The steel for a plastic molding die contains not more
than 0.80 wt % C, not less than 0.01 wt % and less than 1.40 wt %
Si, not less than 0.05 wt % and not more than 2.0 wt % Mn, not less
than 0.005 wt % and not more than 1.00 wt % Ni, not less than 13.0
wt % and not more than 20.0 wt % Cr, not less than 0.20 wt % and
not more than 4.0 wt % Mo+1/2 W, not less than 0.01 wt % and not
more than 1.00 wt % V, not less than 0.36 wt % and not more than
0.80 wt % N, not more than 0.02 wt % O, not more than 0.80 wt % Al,
and the remainder substantially including Fe and unavoidable
impurities.
Inventors: |
Ibuki; Motohiro;
(Nagoya-shi, JP) ; Hamano; Shuji; (Nagoya-shi,
JP) ; Koga; Takeshi; (Nagoya-shi, JP) |
Correspondence
Address: |
C. IRVIN MCCLELLAND;OBLON, SPIVAK, MCCLELLAND, MAIER & NEUSTADT, P.C.
1940 DUKE STREET
ALEXANDRIA
VA
22314
US
|
Assignee: |
DAIDO STEEL CO., LTD.
Nagoya-shi
JP
|
Family ID: |
36636190 |
Appl. No.: |
11/444460 |
Filed: |
June 1, 2006 |
Current U.S.
Class: |
420/61 ; 420/65;
420/67 |
Current CPC
Class: |
C22C 38/46 20130101;
C21D 8/06 20130101; C22C 38/02 20130101; C22C 38/001 20130101; C22C
38/44 20130101; C22C 38/04 20130101; C21D 6/002 20130101; C21D 1/18
20130101; C22C 1/00 20130101; C22C 38/002 20130101; C22C 38/60
20130101; C22C 38/06 20130101 |
Class at
Publication: |
420/061 ;
420/065; 420/067 |
International
Class: |
C22C 38/22 20060101
C22C038/22 |
Foreign Application Data
Date |
Code |
Application Number |
Jun 2, 2005 |
JP |
2005-162823 |
Mar 30, 2006 |
JP |
2006-094094 |
Claims
1. A steel for a plastic molding die comprising: not more than 0.80
wt % C; not less than 0.01 wt % and less than 1.40 wt % Si; not
less than 0.05 wt % and not more than 2.0 wt % Mn; not less than
0.005 wt % and not more than 1.00 wt % Ni; not less than 13.0 wt %
and not more than 20.0 wt % Cr; not less than 0.20 wt % and not
more than 4.0 wt % Mo+1/2 W; not less than 0.01 wt % and not more
than 1.00 wt % V; not less than 0.36 wt % and not more than 0.80 wt
% N; not more than 0.02 wt % O; not more than 0.80 wt % Al; and the
remainder substantially including Fe and unavoidable
impurities.
2. The steel for a plastic molding die according to claim 1 further
comprising at least one element selected from the group consisting
of: not more than 0.030 wt % P; and not more than 0.030 wt % S.
3. The steel for a plastic molding die according to claim 2 further
comprising at least one element selected from the group consisting
of: not less than 0.001 wt % and not more than 0.50 wt % Cu; not
less than 0.001 wt % and not more than 0.50 wt % Co; and not less
than 0.0005 wt % and not more than 0.010 wt % B.
4. The steel for a plastic molding die according to claim 3 further
comprising at least one element selected from the group consisting
of: not less than 0.001 wt % and not more than 0.30 wt % Se; not
less than 0.001 wt % and not more than 0.30 wt % Te; not less than
0.001 wt % and not more than 0.10 wt % Ca; not less than 0.001 wt %
and not more than 0.20 wt % Pb; and not less than 0.001 wt % and
not more than 0.30 wt % Bi.
5. The steel for a plastic molding die according to claim 4 further
comprising at least one element selected from the group consisting
of: not more than 0.20 wt % Ti; not less than 0.001 wt % and not
more than 0.30 wt % Nb; not less than 0.001 wt % and not more than
0.30 wt % Ta; and not less than 0.001 wt % and not more than 0.30
wt % Zr.
6. The steel for a plastic molding die according to claim 3 further
comprising at least one element selected from the group consisting
of: not more than 0.20 wt % Ti; not less than 0.001 wt % and not
more than 0.30 wt % Nb; not less than 0.001 wt % and not more than
0.30 wt % Ta; and not less than 0.001 wt % and not more than 0.30
wt % Zr.
7. The steel for a plastic molding die according to claim 2 further
comprising at least one element selected from the group consisting
of: not less than 0.001 wt % and not more than 0.30 wt % Se; not
less than 0.001 wt % and not more than 0.30 wt % Te; not less than
0.001 wt % and not more than 0.10 wt % Ca; not less than 0.001 wt %
and not more than 0.20 wt % Pb; and not less than 0.001 wt % and
not more than 0.30 wt % Bi.
8. The steel for a plastic molding die according to claim 7 further
comprising at least one element selected from the group consisting
of: not more than 0.20 wt % Ti; not less than 0.001 wt % and not
more than 0.30 wt % Nb; not less than 0.001 wt % and not more than
0.30 wt % Ta; and not less than 0.001 wt % and not more than 0.30
wt % Zr.
9. The steel for a plastic molding die according to claim 2 further
comprising at least one element selected from the group consisting
of: not more than 0.20 wt % Ti; not less than 0.001 wt % and not
more than 0.30 wt % Nb; not less than 0.001 wt % and not more than
0.30 wt % Ta; and not less than 0.001 wt % and not more than 0.30
wt % Zr.
10. The steel for a plastic molding die according to claim 1
further comprising at least one element selected from the group
consisting of: not less than 0.001 wt % and not more than 0.50 wt %
Cu; not less than 0.001 wt % and not more than 0.50 wt % Co; and
not less than 0.0005 wt % and not more than 0.010 wt % B.
11. The steel for a plastic molding die according to claim 10
further comprising at least one element selected from the group
consisting of: not less than 0.001 wt % and not more than 0.30 wt %
Se; not less than 0.001 wt % and not more than 0.30 wt % Te; not
less than 0.001 wt % and not more than 0.10 wt % Ca; not less than
0.001 wt % and not more than 0.20 wt % Pb; and not less than 0.001
wt % and not more than 0.30 wt % Bi.
12. The steel for a plastic molding die according to claim 11
further comprising at least one element selected from the group
consisting of: not more than 0.20 wt % Ti; not less than 0.001 wt %
and not more than 0.30 wt % Nb; not less than 0.001 wt % and not
more than 0.30 wt % Ta; and not less than 0.001 wt % and not more
than 0.30 wt % Zr.
13. The steel for a plastic molding die according to claim 10
further comprising at least one element selected from the group
consisting of: not more than 0.20 wt % Ti; not less than 0.001 wt %
and not more than 0.30 wt % Nb; not less than 0.001 wt % and not
more than 0.30 wt % Ta; and not less than 0.001 wt % and not more
than 0.30 wt % Zr.
14. The steel for a plastic molding die according to claim 1
further comprising at least one element selected from the group
consisting of: not less than 0.001 wt % and not more than 0.30 wt %
Se; not less than 0.001 wt % and not more than 0.30 wt % Te; not
less than 0.001 wt % and not more than 0.10 wt % Ca; not less than
0.001 wt % and not more than 0.20 wt % Pb; and not less than 0.001
wt % and not more than 0.30 wt % Bi.
15. The steel for a plastic molding die according to claim 14
further comprising at least one element selected from the group
consisting of: not more than 0.20 wt % Ti; not less than 0.001 wt %
and not more than 0.30 wt % Nb; not less than 0.001 wt % and not
more than 0.30 wt % Ta; and not less than 0.001 wt % and not more
than 0.30 wt % Zr.
16. The steel for a plastic molding die according to claim 1
further comprising at least one element selected from the group
consisting of: not more than 0.20 wt % Ti; not less than 0.001 wt %
and not more than 0.30 wt % Nb; not less than 0.001 wt % and not
more than 0.30 wt % Ta; and not less than 0.001 wt % and not more
than 0.30 wt % Zr.
Description
BACKGROUND OF THE INVENTION
[0001] 1. Field of the Invention
[0002] The present invention relates to a steel for a plastic
molding die.
[0003] 2. Description of Related Art
[0004] These days, various plastic moldings are used in a variety
of areas. The plastic moldings are generally molded in a desired
shape by the use of, for example, a plastic molding die such as an
injection molding die.
[0005] Incidentally, from the viewpoint of improving strength of
moldings, there is a case that a filler such as glass fiber is
added to a material for the plastic moldings in addition to a resin
being a main ingredient. This sort of additive wears away the die,
lowering dimensional accuracy of plastic moldings to be obtained
and reducing the lifetime of the die.
[0006] In addition, there is a case that the plastic molding
material generates a corrosive gas due to decomposition of the
resin during the course of kneading or the like. When compressed to
be high temperature and high pressure in the die, this sort of
corrosive gas rots the die, giving rise to surface roughness, a
burr and the like in the plastic moldings to be obtained.
[0007] Therefore, for a material for the plastic molding die, it is
necessary to use a metallic material which is excellent in
hardness, wear resistance and corrosion resistance.
[0008] Conventionally, as the metallic material of this sort, there
is known a martensitic stainless steel such as SUS440C and an
improved version thereof.
[0009] In addition, for example, Japanese Patent Gazette No.
3438121 discloses an alloy for a plastic molding die containing
0.25 wt % to 1.0 wt % C, 1.0 wt % maximum Si, 1.6 wt % maximum Mn,
0.10 wt % to 0.35 wt % N, 1.0 wt % maximum Al, 2.8 wt % maximum Co,
14.0 wt % to 25.0 wt % Cr, 0.5 wt % to 3.0 wt % Mo, 3.9 wt %
maximum Ni, 0.04 wt % to 0.4 wt % V, 3.0 wt % maximum W, 0.18 wt %
maximum Nb, and 0.20 wt % maximum Ti, in which the sum of
concentrations of C and N is at least 0.5 wt % and 1.2 wt %
maximum, and the remainder including Fe and unavoidable
impurities.
[0010] However, as the alloy described in the above-mentioned
Japanese Patent Gazette No. 3438121 is prone to generate coarse
crystallized carbonitrides in the manufacturing stage, there arises
a problem, resulting from a difference between hardness of the
generated coarse crystallized carbonitrides and hardness of a
matrix phase of the alloy, that finishing accuracy is unfavorable
as developing unevenness at the time of diesinking working.
[0011] In addition, for the plastic molding die, it is often the
case that the inner surface of the die is mirror polished from the
viewpoint of making states of moldings' surfaces excellent;
however, the alloy described in the above-mentioned Japanese Patent
Gazette No. 3438121 has a problem that mirror polishing properties
are degraded due to the coarse crystallized carbonitrides.
[0012] It sounds logical that the alloy described in the
above-mentioned Japanese Patent Gazette No. 3438121 is made less
prone to generate the coarse crystallized carbonitrides simply by
decreasing the C-content in the alloy; however, decreasing the
C-content causes a problem that wear resistance is decreased.
SUMMARY OF THE INVENTION
[0013] An object of the invention is to overcome the problems
described above and to provide a steel for a plastic molding die
which possesses enough hardness, wear resistance and corrosion
resistance, and is excellent in high-precision processability and
mirror polishing properties.
[0014] To achieve the objects and in accordance with the purpose of
the present invention, a steel for aplastic molding die includes
not more than 0.80 wt % C, not less than 0.01 wt % and less than
1.40 wt % Si, not less than 0.05 wt % and not more than 2.0 wt %
Mn, not less than 0.005 wt % and not more than 1.00 wt % Ni, not
less than 13.0 wt % and not more than 20.0 wt % Cr, not less than
0.20 wt % and not more than 4.0 wt % Mo+1/2 W, not less than 0.01
wt % and not more than 1.00 wt % V, not less than 0.36 wt % and not
more than 0.80 wt % N, not more than 0.02 wt % O, not more than
0.80 wt % Al, and the remainder substantially including Fe and
unavoidable impurities.
[0015] The steel for a plastic molding die consistent with the
present invention is made to have the above-described composition,
in which, especially, the C-content is decreased while the
N-content is increased, so that required hardness is secured.
Accordingly, the steel for a plastic molding die has enough
hardness and wear resistance.
[0016] In addition, the N-content being increased, nitrogen is
solubilized in a matrix phase of the steel and fine carbonitrides
are formed, so that the steel for a plastic molding die is also
excellent in corrosion resistance.
[0017] Further, the C-content being decreased, coarse crystallized
carbonitrides are less prone to generate in the manufacturing
stage. In addition, insoluble carbonitrides at the time of
hardening decrease, and fine carbonitrides obtained by hardening
and tempering are uniformly dispersed, so that the steel for a
plastic molding die is excellent especially in high-precision
processability and mirror polishing properties.
[0018] Additional objects and advantages of the invention are set
forth in the description which follows, are obvious from the
description, or may be learned by practicing the invention. The
objects and advantages of the invention may be realized and
attained by the steel for a plastic molding die in the claims.
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
[0019] A detailed description of one preferred embodiment of a
steel for a plastic molding die embodied by the present invention
is provided below. The steel for a plastic molding die consistent
with the present invention is characterized as containing elements
as provided below, and the remainder substantially including Fe and
unavoidable impurities. Hereinafter, types of the contained
elements, and reasons for specifying their contents are
described.
[0020] (1) C: not more than 0.80 wt %
[0021] C is an element which is necessary for securing strength and
wear resistance, and generates carbides by combining with
carbide-forming elements such as Cr, Mo, W, V and Nb. In addition,
C is an element also necessary for securing hardness by
solubilizing in a matrix phase of the steel at the time of
hardening to form a martensitic structure.
[0022] An excessive content of C, however, increases a tendency to
combine with the above-mentioned carbide-forming elements and a
large amount of carbides are crystallized, so that coarse carbides
come to remain. From the viewpoint of preventing this, the
C-content is specifically not more than 0.80 wt %, preferably not
more than 0.65 wt %, and more preferably less than 0.25 wt %.
[0023] In the present invention, it is desirable to decrease an
amount of the coarse crystallized carbides and an amount of
insoluble carbides at the time of hardening by decreasing the
C-content as much as possible and uniformly disperse fine carbides
obtained by hardening and tempering since hardness can be improved
by increasing a content of N.
[0024] (2) Si: not less than 0.01 wt % and less than 1.40 wt %
[0025] Si functions, similarly to Al to be described later, as a
deoxidation element; however, Al reacts with N and generates AlN to
decrease an amount of N solubilized in the matrix phase and
concurrently the generated coarse AlN degrades high-precision
processability and mirror polishing properties. Accordingly, it is
preferable to use Si as the deoxidation element to reduce a content
of Al in the steel. Specifically, a content of Si is not less than
0.01 wt %, preferably not less than 0.05 wt %, and more preferably
not less than 0.10 wt %.
[0026] An excessive content of Si, however, leads to decline in hot
workability and toughness. From the view point of preventing this,
the Si-content is specifically less than 1.40 wt %, preferably not
more than 0.75 wt %, and more preferably not more than 0.25 wt
%.
[0027] (3) Mn: not less than 0.05 wt % and not more than 2.0 wt
%
[0028] Mn is added as an element for improving hardenability. In
addition, in a case where S is contained unavoidably, Mn is
effective at curbing decline in toughness. A content of Mn is
specifically not less than 0.05 wt %.
[0029] An excessive content of Mn, however, leads to decline in hot
workability, so that the Mn-content is not more than 2.0 wt %.
[0030] (4) Ni: not less than 0.005 wt % and not more than 1.00 wt
%
[0031] Ni increases a solution amount of N. Specifically, a content
of Ni is not less than 0.005 wt %.
[0032] An excessive content of Ni, however, increases residual
austenite to cause changes in dimension with time, so that the
Ni-content is specifically not more than 1.00 wt %.
[0033] (5) Cr: not less than 13.0 wt % and not more than 20.0 wt
%
[0034] Cr increases the solution amount of N while improving
corrosion resistance. In addition, Cr forms carbonitrides.
Specifically, a content of Cr is not less than 13.0 wt %.
[0035] An excessive content of Cr, however, increases a residual
austenite phase even though the steel is subjected to a subzero
treatment, leading to decline in hardness, and also gives a cost
increase. Accordingly, the Cr-content is specifically not more than
20.0 wt %.
[0036] (6) Mo+1/2 W: not less than 0.20 wt % and not more than 4.0
wt %
[0037] Mo and W increase the solution amount of N, and improve
hardenability. In order to obtain these effects, a content of Mo
and W is specifically not less than 0.20 wt % for Mo+1/2 W.
[0038] An excessive content of Mo and W, however, promotes
generation of crystallized carbonitrides to lower an impact value,
so that the content of Mo and W is specifically not more than 4.0
wt % for Mo+1/2 W.
[0039] (7) V: not less than 0.01 wt % and not more than 1.00 wt
%
[0040] V increases the solution amount of N. In addition, V forms
carbonitrides, and by a pin-in effect thereof, crystal grains are
fined to improve strength. Specifically, a content of V is not less
than 0.01 wt %.
[0041] An excessive content of V, however, increases a tendency to
generate coarse carbonitrides, and degrades high-precision
processability and mirror polishing properties. Accordingly, the
V-content is specifically not more than 1.00 wt %.
[0042] (8) N: not less than 0.36 wt % and not more than 0.80 wt
%
[0043] N is an interstitial element which contributes to
improvement in hardness of a martensitic structure. In order to
obtain this effect, a content of N is specifically not less than
0.36 wt %. N of the content can be added by dissolving under
pressure according to Sieverts' law.
[0044] An excessive content of N, however, causes incrassation of N
in solidification, and a blow-hole resulting from N (hereinafter,
referred to as an "N blow") is prone to generate, making it
difficult to curb the N blow by the application of pressure.
Accordingly, the N-content is specifically not more than 0.80 wt
%.
[0045] (9) O: not more than 0.02 wt %
[0046] O is an element which is unavoidably contained in a molten
steel. When a content of O is high, coarse oxides are generated
with Si and Al, and through the mediation of the coarse oxides,
toughness, high-precision processability and mirror polishing
properties are degraded. Accordingly, it is desirable for the
O-content to be low as much as possible. Specifically, the
O-content is not more than 0.02 wt %, and preferably not more than
0.01 wt %.
[0047] (10) Al: not more than 0.80 wt %
[0048] Al functions, similarly to Si, as a deoxidation element;
however, when a content of Al is excessively high, coarse AlN is
prone to generate to degrade high-precision processability and
mirror polishing properties significantly. Accordingly, the
Al-content is specifically not more than 0.80 wt %.
[0049] In addition to the above-described essential elements, the
steel for a plastic molding die consistent with the present
invention may further include one or more than one arbitrary
element selected from the elements cited below. Hereinafter,
reasons for specifying contents of the elements are described.
[0050] <1> P: not more than 0.030 wt % [0051] S: not more
than 0.030 wt %
[0052] P and S are unavoidably contained in the steel. P is
segregated to a crystal grain boundary and S forms sulfides, both
of which lower toughness. Accordingly, contents of P and S are
favorably not more than 0.030 wt %, respectively.
[0053] <2> Cu: not less than 0.001 wt % and not more than
0.50 wt % [0054] Co: not less than 0.001 wt % and not more than
0.50 wt % [0055] B: not less than 0.0005 wt % and not more than
0.010 wt %
[0056] All of Cu, Co and B contribute to improvement in
hardenability. Specifically, a content of Cu is not less than 0.001
wt %, a content of Co is not less than 0.001 wt %, and a content of
B is not less than 0.0005 wt %.
[0057] However, if the contents of Cu, Co and B are made
excessively high, the effect of hardenability is only saturated and
a cost increase is brought about. Accordingly, the Cu-content is
specifically not more than 0.50 wt %, the Co-content is
specifically not more than 0.50 wt %, and the B-content is
specifically not more than 0.010 wt %.
[0058] <3> Se: not less than 0.001 wt % and not more than
0.30 wt % [0059] Te: not less than 0.001 wt % and not more than
0.30 wt % [0060] Ca: not less than 0.001 wt % and not more than
0.10 wt % [0061] Pb: not less than 0.001 wt % and not more than
0.20 wt % [0062] Bi: not less than 0.001 wt % and not more than
0.30 wt %
[0063] Se, Te, Ca, Pb and Bi contribute to improvement in
machinablity. Specifically, a content of Se is not less than 0.001
wt %, a content of Te is not less than 0.001 wt %, a content of Ca
is not less than 0.001 wt %, a content of Pb is not less than 0.001
wt %, and a content of Bi is not less than 0.001 wt %.
[0064] Excessive contents of Se, Te, Ca, Pb and Bi, however, lower
toughness. Accordingly, the Se-content is specifically not more
than 0.30 wt %, the Te-content is specifically not more than 0.30
wt %, the Ca-content is specifically not more than 0.10 wt %, the
Pb-content is specifically not more than 0.20 wt %, and the
Bi-content is specifically not more than 0.30 wt %.
[0065] <4> Ti: not more than 0.20 wt % [0066] Nb: not less
than 0.001 wt % and not more than 0.30 wt % [0067] Ta: not less
than 0.001 wt % and not more than 0.30 wt % [0068] Zr: not less
than 0.001 wt % and not more than 0.30 wt %
[0069] Ti, Nb, Ta and Zr combine with C and N to form
carbonitrides, and contribute to curbed coarsening of crystal
grains. Specifically, a content of Ti is not less than 0.01 wt %, a
content of Nb is not less than 0.001 wt %, a content of Ta is not
less than 0.001 wt %, and a content of Zr is not less than 0.001 wt
%.
[0070] Excessive contents of Ti, Nb, Ta and Zr, however, lower
toughness. Accordingly, the Ti-content is specifically not more
than 0.20 wt %, the Nb-content is specifically not more than 0.30
wt %, the Ta-content is specifically not more than 0.30 wt %, and
the Zr-content is specifically not more than 0.30 wt %.
[0071] In addition, in the above-described steel for a plastic
molding die, it is favorable that a particle size of contained
carbonitrides is not more than 4.0 .mu.m, preferably not more than
3.5 .mu.m, and more preferably not more than 3.0 .mu.m, by which
the steel is made excellent especially in high-precision
processability and mirror polishing properties.
[0072] Incidentally, the particle size of carbonitrides indicates a
representing value such that 90% or more of the total number of
carbonitrides to be observed have particle sizes not larger than
the representing value, when a measuring plane of a
finishing-polished specimen is rotten using a corrosive liquid and
observed through an optical microscope, a scanning electron
microscope or the like.
[0073] Next, description will be given to one example of a
production process of the above-described steel for a plastic
molding die.
[0074] Cited are a production process in which the steel for a
plastic molding die having the above-described composition is
molten by the use of a melting furnace such as a high-frequency
induction furnace capable of applying pressure, and cast into an
ingot or the like, and thereafter, the ingot or the like is
subjected to hot forging or hot rolling to produce a steel material
having necessary dimensions, and the like.
[0075] One example of a heat treatment to which the above-described
steel for a plastic molding die is subjected is as follows.
Specifically, annealing can be performed, for example, by applying
heat in a temperature range of 850.degree. C. to 900.degree. C. for
3 to 5 hours, then providing cooling in a furnace to the vicinity
of 600.degree. C. at a velocity of 10-20.degree. C./hour, and
thereafter providing air-cooling. In addition, specifically,
hardening and tempering can be performed as follows: the hardening
is performed, for example, by applying heat in a temperature range
of 1000.degree. C. to 1200.degree. C. for 0.5 to 1.5 hours and then
providing oil-cooling, and then, the steel is subjected to a
subzero treatment at -196.degree. C. or -76.degree. C. for 0.5 to 1
hour, and thereafter, the tempering is performed by applying heat
in a temperature range of 200.degree. C. to 700.degree. C. for 0.5
to 1.5 hours and then providing air-cooling.
EXAMPLES
[0076] Hereinafter, further detailed description on the present
invention will be given employing and referring to Examples.
[0077] The steels having the chemical compositions listed in Table
1 (the steels consistent with Examples 1 to 16, and the steels
consistent with Comparative Examples 1 to 6) were molten by the use
of a high-frequency induction furnace capable of applying pressure,
and then cast into 50 kg to produce squared bars 60 mm per side
through hot forging. TABLE-US-00001 TABLE 1 C Si Mn P S Ni Cr Mo W
Mo + 1/2W V Al O N Others Example 1 0.80 0.81 0.10 0.017 0.030 1.00
18.1 0.7 1.10 1.25 0.13 0.210 0.015 0.60 Ca = 0.05 Example 2 0.71
1.00 1.70 0.026 0.021 0.53 20.0 0.4 0.20 0.50 0.69 0.440 0.008 0.71
Ti = 0.13 Example 3 0.54 0.45 0.40 0.003 0.005 0.05 17.3 1.1 0.01
1.11 0.03 0.005 0.013 0.36 -- Example 4 0.35 1.30 0.80 0.021 0.011
0.81 16.6 0.5 1.90 1.45 0.44 0.460 0.017 0.41 -- Example 5 0.48
0.69 1.10 0.011 0.023 0.65 13.0 0.1 0.10 0.15 0.25 0.800 0.001 0.47
Nb = 0.10 Example 6 0.60 0.42 0.05 0.030 0.026 0.47 14.6 0.2 3.10
1.75 0.98 0.680 0.012 0.80 Cu = 0.23 Example 7 0.12 0.15 0.40 -- --
0.02 15.2 1.9 0.01 1.91 0.01 0.010 0.005 0.41 -- Example 8 0.42
0.25 1.10 0.023 0.013 0.77 13.7 1.3 0.10 1.35 0.51 0.390 0.020 0.77
Pb = 0.05 Example 9 0.19 0.05 2.00 0.007 0.017 0.17 16.3 0.1 3.90
2.05 0.72 0.570 0.011 0.63 -- Example 10 0.01 0.15 0.50 0.007 0.004
0.50 17.9 1.0 0.01 1.01 0.05 0.150 0.003 0.50 -- Example 11 0.24
0.35 1.30 0.013 0.019 0.23 19.3 0.3 2.10 1.35 0.37 0.560 0.008 0.36
-- Example 12 0.15 0.15 0.30 0.011 0.021 0.21 15.4 0.5 1.30 1.17
0.45 0.230 0.012 0.36 Co = 0.30 Example 13 0.30 0.26 0.20 0.027
0.015 0.43 17.2 0.2 2.40 1.40 0.32 0.460 0.009 0.41 B = 0.007
Example 14 0.10 0.41 0.40 0.023 0.003 0.63 18.3 1.2 0.40 1.43 0.23
0.342 0.006 0.42 Se = 0.10 Te = 0.15 Example 15 0.25 0.23 0.60
0.017 0.007 0.32 14.3 0.8 3.30 2.48 0.69 0.246 0.003 0.36 Ta = 0.21
Zr = 0.14 Example 16 0.15 0.37 0.10 0.006 0.011 0.83 15.6 0.6 0.60
0.90 0.31 0.187 0.001 0.46 Bi = 0.07 Comparative 1.05 0.60 0.40
0.030 0.020 0.05 16.9 0.5 0.01 0.49 0.01 0.020 0.040 0.02 --
Example 1 Comparative 0.37 1.00 0.39 0.011 0.007 0.20 13.5 0.1 0.02
0.11 0.25 0.014 0.012 0.01 -- Example 2 Comparative 0.54 0.45 0.40
0.010 0.020 0.07 17.3 1.1 0.05 1.13 0.05 0.020 0.030 0.20 --
Example 3 Comparative 0.24 0.25 0.32 0.010 0.020 0.05 13.0 0.1 2.30
1.25 0.23 1.000 0.009 0.12 -- Example 4 Comparative 0.63 1.50 1.50
0.015 0.025 0.70 13.2 3.0 2.50 4.25 1.11 0.600 0.020 0.38 --
Example 5 Comparative 0.33 0.50 0.50 0.030 0.070 0.04 15.0 1.0 2.90
2.45 0.13 0.700 0.070 0.40 -- Example 6
[0078] Next, as shown in Table 2, the respective steels consistent
with Examples and Comparative Examples were hardened at a
temperature ranging from 1030.degree. C. to 1150.degree. C.
Further, the steels consistent with Examples 1 to 16 were subjected
to a subzero treatment at -76.degree. C. or -196.degree. C. and
then, tempered at a temperature ranging from 200.degree. C. to
475.degree. C. Properties of specimens consistent with Examples and
Comparative Examples were assessed as follows. TABLE-US-00002 TABLE
2 Hardening Tempering Subzero temperature temperature treatment
Example1 1030.degree. C. 200.degree. C. -196.degree. C. Example2
1030.degree. C. 200.degree. C. -196.degree. C. Example3
1030.degree. C. 200.degree. C. -76.degree. C. Example4 1030.degree.
C. 200.degree. C. -196.degree. C. Example5 1030.degree. C.
200.degree. C. -76.degree. C. Example6 1100.degree. C. 450.degree.
C. -76.degree. C. Example7 1100.degree. C. 450.degree. C.
-196.degree. C. Example8 1150.degree. C. 450.degree. C.
-196.degree. C. Example9 1100.degree. C. 400.degree. C. -76.degree.
C. Example10 1100.degree. C. 400.degree. C. -76.degree. C.
Example11 1150.degree. C. 400.degree. C. -196.degree. C. Example12
1050.degree. C. 300.degree. C. -196.degree. C. Example13
1075.degree. C. 250.degree. C. -76.degree. C. Example14
1100.degree. C. 400.degree. C. -196.degree. C. Example15
1150.degree. C. 475.degree. C. -196.degree. C. Example16
1075.degree. C. 200.degree. C. -76.degree. C. Comparative
1030.degree. C. 200.degree. C. not performed Example 1 Comparative
1030.degree. C. 200.degree. C. not performed Example 2 Comparative
1030.degree. C. 200.degree. C. not performed Example 3 Comparative
1030.degree. C. 200.degree. C. not performed Example 4 Comparative
1030.degree. C. 200.degree. C. not performed Example 5 Comparative
1030.degree. C. 200.degree. C. not performed Example 6
<Particle Size of Carbonitrides>
[0079] 15 cubic millimeters of blocks were cut from the respective
squared bars and subjected to the heat treatments, and then
measuring planes thereof were polished using emery paper of #1500.
Then, the measuring planes were finished by buffing using diamond
paste of 1 .mu.m and rotten using a villela etching liquid. Then,
the measuring planes were photographed using an optical microscope
(magnification: 400.times., with 10.times. eyepieces), and a value,
such that 90% or more of the total number of carbonitrides to be
observed had particle sizes not larger than the value, was defined
as a representing value. The one whose carbonitrides had the
particle size not more than 4.0 .mu.m was regarded as passed.
<Hardness>
[0080] 10 cubic millimeters of blocks were cut from the respective
squared bars and subjected to the heat treatments, and then
measuring planes and ground planes thereof were polished using
emery paper of #400. Then, hardness of the blocks was measured
using a Rockwell C scale, and the one having the hardness of not
less than HRC55 was regarded as passed.
<Wear Resistance>
[0081] Wear resistance was assessed using a pin-on-disk friction
and wear tester. Specifically, two pins 8 mm in diameter were cut
from the respective squared bars and subjected to the heat
treatments, and a disk which was cut from S45C was used. Test
conditions were as follows: a slipping velocity; 1.6 m/s, a
slipping distance; 5,000 m, a pressing load; 10.5 kgf, and
lubrication oil; not used. Before and after the test, weights of
the pins were measured, and thereby weights of wear were measured.
Besides, in Table 3, listed are the ratios of the wear weights of
the steels consistent with Examples and Comparative Examples except
Comparative Example 1, to the wear weight of the steel consistent
with Comparative Example 1 (SUS440C), which is assumed to be 100.
The one with the ratio which was below 130 was regarded as
passed.
<Corrosion Resistance>
[0082] Rods 15 mm in diameter and 60 mm in length were made from
the respective squared bars, subjected to the heat treatments, and
then surfaces of which were finished using emery paper of #400.
Then, based on JIS Z2371, a salt spray test was performed to check
the formation of rust. Besides, in Table 3, the one which formed no
rust was defined as A, the one which slightly formed rust was
defined as B, the one which considerably formed rust was regarded
as C, and the one which formed rust overall was defined as D, and
the one which is A or B was regarded as passed.
<High-Precision Processability>
[0083] Specimens of 60 mm.times.60 mm.times.100 mm were prepared
from the respective squared bars, and machined using a solid
carbide end mill (with six flutes) of 10 mm in diameter as a tool
under the conditions of cutting speed of 120 m/min., feed speed of
0.06 mm/rev., the width of cut of 0.5 mm, and the height of cut of
10 mm. Then, based on JIS B0633, the maximum surface roughness
R.sub.y of machined surfaces thereof was measured. At this time,
the one whose maximum surface roughness R.sub.y was not more than
2.0 .mu.m was regarded as passed.
<Mirror Polishing Properties>
[0084] Plates of 50 mm.times.45 mm.times.12 mm were made from the
respective squared bars, subjected to the heat treatments, and then
polished by a machine using a grinding stone of # 14000. Then, the
plates were subjected to chemical etching and specimens were
prepared. After that, based on JIS B0633, surface roughness R.sub.a
of the specimens was measured. At this time, the one whose surface
roughness R.sub.a was not more than 0.05 .mu.m was regarded as
passed.
[0085] Assessment results of the properties are shown in Table 3.
TABLE-US-00003 TABLE 3 Particle size of High-precision Mirror
polishing carbonitrides Hardness Wear resistance Corrosion
processability properties (.mu.m) (HRC) (Wear resistance ratio)
resistance (Ry: .mu.m) (Ra: .mu.m) Example 1 2.6 61.3 105 B 1.42
0.0298 Example 2 2.5 61.2 103 B 1.43 0.0286 Example 3 2.7 61.0 109
B 1.41 0.0275 Example 4 2.6 58.7 114 B 1.40 0.0281 Example 5 2.8
59.6 109 B 1.40 0.0286 Example 6 2.3 62.2 105 B 1.39 0.0274 Example
7 2.7 59.0 126 B 1.37 0.0252 Example 8 2.9 60.6 103 B 1.38 0.0277
Example 9 2.4 59.7 106 B 1.37 0.0263 Example 10 2.1 55.4 124 A 1.37
0.0266 Example 11 2.6 58.8 112 B 1.36 0.0256 Example 12 2.2 58.2
102 B 1.35 0.0284 Example 13 2.4 60.3 102 B 1.37 0.0272 Example 14
2.5 57.6 112 B 1.43 0.0268 Example 15 2.4 59.6 107 B 1.37 0.0256
Example 16 2.5 59.3 104 B 1.42 0.0274 Comparative 8.2 60.2 100 C
2.56 0.0544 Example 1 Comparative 3.5 52.0 133 B 1.68 0.0304
Example 2 Comparative 5.8 58.2 115 B 2.49 0.0295 Example 3
Comparative 4.2 52.2 131 B 2.45 0.0311 Example 4 Comparative 7.8
59.6 102 B 2.51 0.5620 Example 5 Comparative 8.5 58.1 105 A 2.48
0.0525 Example 6
[0086] According to Table 3, it is apparent that in the steel
consistent with Comparative Example 1, there exist coarse
crystallized carbonitrides, so that it is inferior in
high-precision processability and mirror polishing properties. It
is also inferior in corrosion resistance.
[0087] In addition, the steels consistent with Comparative Examples
2 and 4 have a content of N smaller than the specified value of the
present invention, so that they cannot obtain enough hardness and
is inferior in wear resistance.
[0088] In addition, the steel consistent with Comparative Example 3
has a content of O larger than the specified value of the present
invention, so that it forms coarse oxides. In addition, the steel
consistent with Comparative Example 4 has a content of Al larger
than the specified value of the present invention, so that it forms
coarse AlN. Accordingly, they are inferior in high-precision
processability.
[0089] In addition, the steel consistent with Comparative Example 5
has a content of V larger than the specified value of the present
invention, so that it forms coarse VN. Accordingly, it is inferior
in high-precision processability and mirror polishing
properties.
[0090] In addition, the steel consistent with Comparative Example 6
has a content of O larger than the specified value of the present
invention, so that it forms coarse oxides. Accordingly, it is
inferior in high-precision processability and mirror polishing
properties.
[0091] It was shown that, in contrast to the steels consistent with
Comparative Examples 1 to 6, all of the steels consistent with
Examples 1 to 16 according to the present invention possess enough
hardness, wear resistance and corrosion resistance, and are
excellent in high-precision processability and mirror polishing
properties.
[0092] Therefore, it can be said that the steels consistent with
the present invention are favorably employed as a material for a
plastic molding die.
[0093] The foregoing description of the preferred embodiments of
the invention has been presented for purposes of illustration and
description. It is not intended to be exhaustive or to limit the
invention to the precise form disclosed, and modifications and
variations are possible in the light of the above teachings or may
be acquired from practice of the invention. The embodiments chosen
and described in order to explain the principles of the invention
and its practical application to enable one skilled in the art to
utilize the invention in various embodiments and with various
modifications as are suited to the particular use contemplated. It
is intended that the scope of the invention be defined by the
claims appended hereto, and their equivalents.
* * * * *