JP3353321B2 - Method for producing Fe-Ni alloy sheet for shadow mask excellent in press formability and Fe-Ni alloy sheet for shadow mask excellent in press formability - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an Fe-Ni alloy sheet having excellent press formability, and more particularly to a preferable Fe-Ni alloy sheet for a shadow mask used for a color cathode ray tube and a method for producing the same. .

[0002]

2. Description of the Related Art In recent years, with the high quality of color televisions,
As an alloy for a shadow mask that can cope with the problem of color misregistration, an Fe-Ni-based alloy containing 34 to 38 wt% of Ni (hereinafter referred to as "conventional Fe-Ni-based alloy") is used. This conventional Fe-Ni alloy has a significantly lower coefficient of thermal expansion than low carbon steel conventionally used as a shadow mask material. Therefore, if a shadow mask is made of a conventional Fe-Ni alloy, even if the shadow mask is heated by an electron beam, the problem of color shift due to thermal expansion of the shadow mask hardly occurs.

[0003] An alloy sheet for a shadow mask is usually manufactured by the following steps. That is, an alloy ingot is prepared by a continuous casting method or an ingot-making method, and then, into the alloy ingot thus prepared, slab rolling, hot rolling, and cold rolling.
Annealing is performed to produce an alloy thin plate.

[0004] The alloy sheet for a shadow mask manufactured as described above is usually processed into a shadow mask by the following steps. That is, a hole for passing an electron beam (hereinafter, referred to as a hole) is formed on a thin alloy plate for shadow mask by photoetching.
(Hereinafter simply referred to as “holes”) (hereinafter, the thin alloy plate for a shadow mask that has been perforated by etching is referred to as a “flat mask”), and then the flat mask is annealed, and then the annealed flat mask is removed. Then, it is press-formed into a curved shape so as to conform to the shape of a cathode ray tube, and then, this is assembled into a shadow mask, and a blackening process is performed on the surface thereof.

However, when such a conventional Fe-Ni alloy is used, the strength is higher than that of a conventional low carbon steel shadow mask material, and the alloy is cold-rolled, recrystallized, annealed or re-crystallized. The material for shadow masks manufactured by minor finish rolling after crystal annealing should be softened and annealed at a temperature of 800 ° C. or more before press forming due to the problem of press formability after etching perforation to coarsen the crystal grains. To achieve softening. After this softening annealing, spherical molding was performed by a method of warm pressing.

However, even at 800 ° C., the temperature is high,
From the viewpoint of work efficiency and economy, it is desired to develop a manufacturing method capable of obtaining a low strength equivalent to that of a material annealed at a temperature of 800 ° C. or higher by softening annealing at a lower temperature than the current one. Thus, the following prior art is known. That is, JP-A-3-267320 discloses that, after cold rolling and subsequent recrystallization annealing, finish cold rolling is performed in a rolling reduction range of 5 to 20%, so that a temperature of less than 800 ° C., specifically, At 730 ° C for 60 min.
With a 0.2% proof stress of 9.5 kgf / mm ² (10 kgf / mm ² or less), the strength is reduced to a level at which press formability is good.

[0007]

However, in the above-mentioned prior art, the strength is reduced to a satisfactory level of the press formability under annealing conditions of 730 ° C. for 60 minutes. It was not enough to satisfy all the warm press forming qualities. That is, in the shadow mask material according to the above-described technique, the mold was seized at the time of molding, and cracks were easily generated at the shadow mask end.

[0008] Despite these problems, CRT manufacturers have been working to further pursue work efficiency and economy.
Attempts have also been made to shorten the annealing time before pressing at the above-mentioned temperatures. Incidentally, the annealing time is specifically 40 minutes or less, and in some cases, it may be a short processing such as 2 minutes. When such annealing conditions are applied to the above-described prior art, the occurrence of galling on the mold during press molding becomes more remarkable, and the shadow mask is frequently cracked, which is a serious problem in quality.

The present invention has been made in view of the above-mentioned circumstances, and has been devised through repeated studies. The present invention is excellent in press formability, annealing at a low temperature of 720 ° C. to 790 ° C. and as short as 40 minutes or less. It has succeeded in providing an Fe-Ni-based Invar alloy thin plate for a shadow mask and a method for producing the same, which can provide the required press-forming quality even in the annealing time, and is as follows. The press molding quality of the above means that the shape can be easily frozen at the time of molding, that it has good compatibility with the mold (no galling with the mold), and that no cracking of the material occurs.

[0010] In wt%, it contains 34-38% of Ni:
0.05% or less, B: 0.0005% or less, O: 0.0002
% Or less, and N: 0.0015% or less. A hot-rolled steel strip of a low-thermal-expansion alloy, which is hot-rolled, is subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. In manufacturing in the process, the hot-rolled sheet annealing is performed at 910 to 990 ° C,
The rolling reduction (R)% in the finish cold rolling is performed within the range of the region I shown in FIG. 3 in accordance with the austenite grain size D (μm) after the recrystallization annealing described above. The temperature (T ° C) is 720 to 790 ° C, and the time (tmin) is 2 to 4
By applying it under the conditions satisfying 0 min and T ≧ -53.8 logt + 806, the 0.2% proof stress of the alloy plate after annealing is 28.5 kgf / mm ² or less and the degree of integration of {211} crystal plane is 16% or less. A method for producing an Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability, characterized by being adjusted.

[0011] A hot-rolled steel strip of a low thermal expansion alloy having the component described in 0010 is subjected to hot-rolled sheet annealing, then cold rolling and subsequent recrystallization annealing, and then subjected to finish cold rolling. When performing the hot rolled sheet annealing at 910 ° C.
It is performed at 990 ° C, and the rolling reduction (R%) in the finish cold rolling is as follows:
Austenite grain size D (μm) after recrystallization annealing
In the area II shown in FIG.
The temperature (T ° C.) of the annealing before press forming is 720 to 790.
° C, time (tmin) is 2 to 40 min and T ≧ -53.8 log
By applying under conditions satisfying t + 806, the 0.2% proof stress of the annealed alloy plate is adjusted to 28.0 kgf / mm ² or less, and the degree of integration of the {211} crystal plane is adjusted to 16% or less. Fe for shadow masks with excellent press formability
-Manufacturing method of Ni alloy sheet.

[0012] A hot-rolled steel strip of a low thermal expansion alloy having the component described in 0010 is subjected to hot-rolled sheet annealing, then cold rolling and subsequent recrystallization annealing, and then subjected to finish cold rolling. When performing the hot rolled sheet annealing at 910 ° C.
It is performed at 990 ° C, and the rolling reduction (R%) in the finish cold rolling is as follows:
Austenite grain size D (μm) after recrystallization annealing
In the subsequent annealing before press forming, the temperature (T ° C.) is 720 to 7
90 ° C., time (tmin) is 2 to 40 min and T ≧ −53.8
By applying under conditions satisfying log t + 806, the 0.2% proof stress of the annealed alloy plate is 27.5 kgf / mm ² or less,
A method for producing an Fe-Ni alloy sheet for a shadow mask having excellent press formability, wherein the degree of integration of {211} crystal planes is adjusted to 16% or less.

[0013] The step of subjecting a hot-rolled steel strip of a low-thermal-expansion alloy having the component described in 0010 to hot-rolled sheet annealing, then performing cold rolling and subsequent recrystallization annealing, and then performing finish cold rolling. In the production, the hot-rolled sheet annealing is performed at 910 to 990 ° C., and the rolling reduction (R)% in the finish cold rolling is determined according to the austenite grain size D (μm) after the recrystallization annealing described above.
The temperature (T ° C.) is 720-790 ° C., the time (tmin) is 2-40 min, and T ≧ −53.8 logt + 80.
6, the 0.2% proof stress of the annealed alloy sheet is 28.5 kgf / mm ² or less, and
1) A method for producing an Fe-Ni alloy sheet for a shadow mask excellent in press formability, wherein the degree of integration of crystal planes is adjusted to 16% or less.

[0014] A hot-rolled steel strip of a low thermal expansion alloy having the components described in 0010 is subjected to hot-rolled sheet annealing, then cold rolling and subsequent recrystallization annealing, and then subjected to finish cold rolling. When performing the hot rolled sheet annealing at 910 ° C.
It is performed at 990 ° C, and the rolling reduction (R%) in the finish cold rolling is as follows:
Austenite grain size D (μm) after recrystallization annealing
3 is performed within the range of region II shown in FIG.
90 ° C., time (tmin) is 2 to 40 min and T ≧ −53.8
By applying under the condition satisfying logt + 806, the 0.2% proof stress of the alloy plate after annealing is 28.0 kgf / mm ² or less,
A method for producing an Fe-Ni alloy sheet for a shadow mask having excellent press formability, wherein the degree of integration of {211} crystal planes is adjusted to 16% or less.

A hot-rolled steel strip of a low-thermal-expansion alloy having the components described in 0010 is subjected to hot-rolled sheet annealing, then to cold rolling and subsequent recrystallization annealing, and then to finish cold rolling. When performing the hot rolled sheet annealing at 910 ° C.
It is performed at 990 ° C, and the rolling reduction (R%) in the finish cold rolling is as follows:
Austenite grain size D (μm) after recrystallization annealing
In the range III shown in FIG. 3, the annealing after the etching and before the press forming is performed at a temperature (T ° C.) of 72 ° C.
0 to 790 ° C, time (tmin) is 2 to 40 min and T ≧ −
By applying under conditions that satisfy 53.8 log t + 806, the 0.2% proof stress of the annealed alloy sheet is 27.5 kgf / mm ^2.
A method for producing an Fe—Ni alloy sheet for a shadow mask having excellent press formability, wherein the degree of integration of {211} crystal planes is adjusted to 16% or less.

[0016] The step of subjecting a hot-rolled steel strip of a low thermal expansion alloy having the component described in 0010 to hot-rolled sheet annealing, then performing cold rolling and subsequent recrystallization annealing, and then performing finish cold rolling. In the production, the hot-rolled sheet annealing is performed at 910 to 990 ° C., and the rolling reduction (R)% in the finish cold rolling is determined according to the austenite grain size D (μm) after the recrystallization annealing described above.
And the subsequent annealing before press forming is performed under the conditions that the temperature (T ° C.) is 720 to 790 ° C., the time (tmin) is 2 to 40 min, and T ≧ −53.8 logt + 806. 0.2 in the alloy plate after annealing
% Proof stress is adjusted to 28.5 kgf / mm ² or less, and the degree of integration of {211} crystal planes is adjusted to 16% or less, and then etching is performed. Manufacturing method of Ni alloy sheet.

A hot-rolled steel strip of a low thermal expansion alloy having the components described in 0010 is subjected to hot-rolled sheet annealing, then to cold rolling and subsequent recrystallization annealing, and then to finish cold rolling. When performing the hot rolled sheet annealing at 910 ° C.
It is performed at 990 ° C, and the rolling reduction (R%) in the finish cold rolling is as follows:
Austenite grain size D (μm) after recrystallization annealing
In the area II shown in FIG.
The temperature (T ° C.) of the annealing before press forming is 720 to 790.
° C, time (tmin) is 2 to 40 min and T ≧ -53.8 log
By applying under the condition satisfying t + 806, the 0.2% proof stress of the alloy plate after annealing is adjusted to 28.0 kgf / mm ² or less and the degree of integration of the {211} crystal plane is adjusted to 16% or less.
A method for producing a Fe—Ni alloy thin plate for a shadow mask having excellent press formability, characterized by performing etching.

[0018] A hot-rolled steel strip of a low thermal expansion alloy having the component described in 0010 is subjected to hot-rolled sheet annealing, then cold rolling and subsequent recrystallization annealing, and then subjected to finish cold rolling. When performing the hot rolled sheet annealing at 910 ° C.
It is performed at 990 ° C, and the rolling reduction (R%) in the finish cold rolling is as follows:
Austenite grain size D (μm) after recrystallization annealing
In the subsequent annealing before press forming, the temperature (T ° C.) is 720 to 7
90 ° C., time (tmin) is 2 to 40 min and T ≧ −53.8
By applying under conditions satisfying log t + 806, the 0.2% proof stress of the annealed alloy plate is 27.5 kgf / mm ² or less,
A method for producing a Fe-Ni alloy thin plate for a shadow mask having excellent press formability, wherein etching is performed after adjusting the degree of integration of {211} crystal planes to 16% or less.

A low-thermal-expansion alloy having the component described in 0010 is directly cast on a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. In doing so, the annealing of the thin cast plate is performed at 910 to 990
C., and the rolling reduction (R)% in the finish cold rolling is performed within the range of the region I shown in FIG. 3 according to the austenite grain size D (μm) after the above-mentioned recrystallization annealing. In the previous annealing, the temperature (T ° C) is 720 to 790 ° C, and the time (tm
n) is 2 to 40 min and T ≧ −53.8 logt + 806 is applied to the alloy plate after annealing so that
Fe-Ni alloy sheet for shadow mask excellent in press formability, characterized in that the 0.2% proof stress is adjusted to 28.5 kgf / mm ² or less and the degree of integration of {211} crystal planes is adjusted to 16% or less. Manufacturing method.

The low thermal expansion alloy having the component described in 0010 is directly cast on a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. At this time, the annealing of the thin cast plate is performed at 910
Degree of reduction (R%) in cold rolling at finish
Is the austenite grain size D (μ)
m) is performed within the range of the region II shown in FIG. 3, and the subsequent annealing before press forming is performed at a temperature (T ° C.) of 720 to 79 ° C.
0 ° C., time (tmin) is 2 to 40 min and T ≧ −53.8 lo
By applying under conditions satisfying gt + 806, the 0.2% proof stress of the annealed alloy plate is adjusted to 28.0 kgf / mm ² or less, and the degree of integration of {211} crystal planes is adjusted to 16% or less. For shadow masks with excellent press moldability
Manufacturing method of Fe-Ni alloy sheet.

A low-thermal-expansion alloy having the components described in 0010 is directly cast on a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. At this time, the annealing of the thin cast plate is performed at 910
Degree of reduction (R%) in cold rolling at finish
Is the austenite grain size D (μ)
m) within the range shown in the area III shown in FIG.
Subsequently, the temperature (T ° C.) of the annealing before press forming is 720.
７790 ° C., time (tmin) is 2-40 min and T ≧ −5
By applying under the condition that satisfies 3.8 log t + 806,
A shadow mask excellent in press formability, characterized in that the 0.2% proof stress of the alloy plate after annealing is adjusted to 27.5 kgf / mm ² or less and the degree of integration of {211} crystal faces is adjusted to 16% or less. Of manufacturing Fe-Ni alloy sheet for use.

A low-thermal-expansion alloy having the components described in 0010 is directly cast on a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. In doing so, the annealing of the thin cast plate is performed at 910 to 990
C., and the rolling reduction (R)% in the finish cold rolling is performed within the range of the region I shown in FIG. 3 according to the austenite grain size D (μm) after the recrystallization annealing. The temperature (T ° C) of the annealing before forming is 720 to 790 ° C,
The time (tmin) is 2 to 40 min and T ≧ -53.8 logt +
By applying under the conditions satisfying 806, the 0.2% proof stress of the annealed alloy plate is adjusted to 28.5 kgf / mm ² or less and the degree of integration of the {211} crystal plane is adjusted to 16% or less. Fe for shadow mask with excellent press moldability
-Manufacturing method of Ni alloy sheet.

The low-thermal-expansion alloy having the component described in 0010 is directly cast on a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. At this time, the annealing of the thin cast plate is performed at 910
Degree of reduction (R%) in cold rolling at finish
Is the austenite grain size D (μ)
m) is performed within the range of the region II shown in FIG.
７790 ° C., time (tmin) is 2-40 min and T ≧ −5
By applying under conditions that satisfy 3.8 logt + 806,
A shadow mask excellent in press formability, characterized in that the alloy plate after annealing has a 0.2% proof stress of 28.0 kgf / mm ² or less and the degree of integration of {211} crystal faces is adjusted to 16% or less. Of manufacturing Fe-Ni alloy sheet for use.

The low-thermal-expansion alloy having the component described in 0010 is directly cast on a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. At this time, the annealing of the thin cast plate is performed at 910
Degree of reduction (R%) in cold rolling at finish
Is the austenite grain size D (μ)
m) within the range shown in the area III shown in FIG.
The temperature (T ° C.) of the annealing before the press forming after the etching process is 720 to 790 ° C., and the time (tmin) is 2 to 40 min and T
By applying under the condition that ≧ −53.8 log t + 806, the 0.2% proof stress of the annealed alloy sheet is 27.5 kgf / m.
A method for producing an Fe—Ni alloy sheet for a shadow mask having excellent press formability, wherein the degree of integration of {211} crystal planes is adjusted to 16% or less and m ² or less.

[0025] A low thermal expansion alloy having the component described in 0010 is directly cast on a thin cast plate, annealed, cold rolled, followed by recrystallization annealing, and then subjected to finish cold rolling. In doing so, the annealing of the thin cast plate is performed at 910 to 990
C., and the rolling reduction (R)% in the finish cold rolling is performed within the range of the region I shown in FIG. 3 according to the austenite grain size D (μm) after the above-mentioned recrystallization annealing. In the previous annealing, the temperature (T ° C) is 720 to 790 ° C, and the time (tm
n) is 2 to 40 min and T ≧ −53.8 logt + 806 is applied to the alloy plate after annealing so that
A shadow mask excellent in press moldability, characterized in that a 0.2% proof stress is 28.5 kgf / mm ² or less and an etching process is performed after adjusting the degree of integration of {211} crystal faces to 16% or less. Manufacturing method of Fe-Ni alloy sheet.

A low thermal expansion alloy having the components described in 0010 is directly cast on a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. At this time, the annealing of the thin cast plate is performed at 910
Degree of reduction (R%) in cold rolling at finish
Is the austenite grain size D (μ)
m) is performed within the range of the region II shown in FIG. 3, and the subsequent annealing before press forming is performed at a temperature (T ° C.) of 720 to 79 ° C.
0 ° C., time (tmin) is 2 to 40 min and T ≧ −53.8 lo
gt + 806, the alloy plate after annealing is adjusted to have a 0.2% proof stress of 28.0 kgf / mm ² or less and a {211} crystal plane integration degree of 16% or less. A method for producing an Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability, characterized by performing the following.

A low-thermal-expansion alloy having the components described in 0010 is directly cast on a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. At this time, the annealing of the thin cast plate is performed at 910
Degree of reduction (R%) in cold rolling at finish
Is the austenite grain size D (μ)
m) within the range shown in the area III shown in FIG.
Subsequently, the temperature (T ° C.) of the annealing before press forming is 720.
７790 ° C., time (tmin) is 2-40 min and T ≧ −5
By applying under the condition that satisfies 3.8 log t + 806,
Press formability characterized by adjusting the 0.2% proof stress of the annealed alloy plate to 27.5 kgf / mm ² or less and adjusting the degree of integration of {211} crystal planes to 16% or less and then performing etching. Method of manufacturing Fe-Ni alloy sheet for shadow mask with excellent performance.

% By weight, containing 34-38% of Ni:
0.05% or less, B: 0.000001 to 0.0001%, O:
0.0020% or less, N: 0.0015% or less, C: 0.00
Fe is 50% or less, Mn is 0.35% or less, Cr is 0.05% or less, and Fe is composed of the remaining unavoidable impurities and the composition of Fe.
-Ni-based alloy, and the 0.2% proof stress of the alloy sheet before press forming and after annealing is 28.5 kgf / mm ² or less, and the degree of integration of the {221} crystal plane is 15% or less. Fe-N for shadow masks with excellent press moldability
i alloy sheet.

[0029]

The present invention as described above will be further described. From the above-mentioned viewpoint, the present inventors have made intensive studies in order to develop Fe-Ni-based alloy thin plates for shadow masks having excellent press molding quality. As a result, the following findings were obtained. That is, the present invention achieves the required press-forming quality by adjusting the chemical composition of the Fe-Ni alloy thin plate for a shadow mask, and further, the 0.2% proof stress and the crystal orientation within a predetermined range. It is.

More specifically, the content of B and O within a predetermined range enhances the growth of crystal grains during annealing before pressing under the conditions characteristic of the present invention, and lowers the yield strength by coarsening. Then, by containing Si and N in a predetermined range, the conformity with the mold at the time of press molding is improved (the occurrence of galling on the mold is suppressed), and further, the alloy thin plate after the pre-press annealing is obtained. 2
By setting the degree of integration of the 11 ° crystal plane within a predetermined range, the occurrence of cracks in the material during press forming can be suppressed.

The present inventors have obtained the following findings. That is, in the production process of the present alloy, the hot-rolled steel strip is subjected to hot-rolled sheet annealing at a predetermined temperature before being cold-rolled, and further, the rolling reduction in the finish cold-rolling is performed before the finish cold-rolling. By appropriately changing the grain size of austenite, the 0.2% proof stress and the degree of integration of the {211} crystal plane of the alloy sheet after the pre-press annealing can be adjusted within a predetermined range.

The present invention has been made based on the above-mentioned findings. The following describes the chemical composition of the Fe—Ni-based alloy sheet for a shadow mask according to the present invention, and 0.2% after annealing before press. The reasons for limiting the percent proof stress and the degree of integration of crystal planes are as follows.

(1) Nickel: Fe-Fe for a shadow mask is used to prevent the occurrence of color misregistration.
The upper limit of the average thermal expansion coefficient in the temperature range of 30 to 100 ° C. required for Ni-based alloy thin plates is about 2.0 × 10 ⁻⁶ / ° C.
It is. The coefficient of thermal expansion depends on the nickel content of the alloy sheet. The range of the nickel content satisfying the above-mentioned condition of the average thermal expansion coefficient is in the range of 34 to 38 wt%. Therefore, the nickel content is 34-38 wt.
It should be limited to the range of%.

In the present invention, the yield strength required for improving the shape freezing property at the time of press forming and suppressing the occurrence of cracks in the alloy sheet is based on the premise that warm pressing is performed.
The upper limit was 28.5 kgf / mm ² at 0.2% proof stress at room temperature. Even if the 0.2% proof stress is 28.5 kgf / mm ² or less, the shape freezing property can be further improved by reducing the 0.2% proof stress.

In order to suppress other press forming qualities intended in the present invention, that is, to suppress the occurrence of cracks in the material, it is necessary to maintain the above-mentioned yield strength and to apply the ｛211抑制 す る It is essential to suppress the degree of integration of crystal planes to a specific value.

First, in order to increase the growth of crystal grains under the annealing conditions before pressing intended in the present invention, O and B are controlled to specific values or less, and the familiarity of the mold during press forming is improved. For this purpose, it is necessary to control Si and Ni to a specific value or less, respectively, as follows.

(2) Oxygen: Oxygen is one of the impurities unavoidably mixed into the present alloy. When the oxygen content increases, the number of oxide-based nonmetallic inclusions in the alloy increases.
The growth of crystal grains during annealing before press forming at 790 ° C. for a time of 40 minutes or less is inhibited. That is, this O amount is 0.
If it exceeds 0020%, the above-mentioned effect of inhibiting grain growth becomes remarkable, and a 0.2% proof stress of 28.5 kgf / mm ² or less cannot be obtained after annealing before press forming. did.

(3) Boron: Boron improves hot workability in the present alloy, but when the content is large, boron segregates at the grain boundaries of recrystallized grains formed at the time of annealing before pressing. Is difficult to move, and as a result, the growth of crystal grains is hindered, and the required 0.2% proof stress cannot be obtained after annealing before press forming. In particular, under the annealing conditions before pressing specified in the present invention, such an effect of inhibiting the growth of grains is strong, and this action does not work uniformly for all the crystal grains, resulting in remarkable mixed grain size. It shows the structure, and causes unevenness in elongation of the material during press molding.

In the case of B, the degree of integration of {211} crystal planes, which cause cracking of the material skirt, is also increased after annealing. If the B content exceeds 0.0005%, the above-described inhibitory effect on the grain growth becomes remarkable, and 0.2 of 28.5 kgf / mm ² or less.
% Yield strength cannot be obtained, and problems such as uneven elongation during pressing occur, and the degree of integration of {211} crystal planes exceeds the upper limit specified in the present invention. From the above, the upper limit of B amount is
0.0005%.

(4) Silicon: Silicon is used as a deoxidizing element when the present alloy is melted, but if it exceeds 0.05%, an oxide film of Si is formed on the surface of the alloy during annealing before pressing, The oxide film deteriorates the conformity with the mold during press molding, and the alloy is liable to the mold. Therefore, the upper limit of the Si content is set to 0.05%. Even if the content of Si is 0.05% or less, the familiarity between the alloy plate and the mold can be further improved by further reducing the amount of Si.

(5) Nitrogen: Nitrogen is an element that is inevitably mixed when the present alloy is melted. If it exceeds 0.0015%, N is concentrated on the alloy surface during annealing before pressing, and this alloy surface Due to the nitride, the conformity with the mold at the time of press molding is deteriorated, and the alloy plate is apt to bite the mold. Therefore, the upper limit of the N amount is set to 0.0015%.

The invar alloy for a shadow mask according to the present invention has a specific composition of B, O, Si, N in the basic composition of Fe—Ni as described above, and 0.2 after annealing before press.
% Proof stress is 28.5 kgf / mm ² or less and the degree of integration of {211} crystal faces is 16% or less. In addition to the above composition, C: 0.0050% or less, Mn: 0 It is preferable that the content is within the range of 0.35% or less and Cr: 0.05% or less.

By controlling the components as described above and setting the 0.2% proof stress after the pre-press annealing within the provisions of the present invention, galling of the alloy during press forming into a mold is suppressed,
In addition, it is possible to achieve an excellent level of shape freezing property, but cracking of the material still poses a problem in press molding quality. In order to solve such a problem, the inventors of the present invention varied the components within the specifications of the present invention and the crystal orientation of the present alloy plate having a 0.2% proof stress by changing the orientation of the material during press forming. And examined the relationship. As a result, in order to suppress cracking of the present alloy material, it is necessary to reduce the thickness of the alloy plate after annealing before pressing.
It has been found that it is effective to control the degree of integration of {211} crystal planes to a specific value or less in addition to the regulation of 2% proof stress.

FIG. 1 shows the relationship between alloy plate cracking during press forming, the degree of integration of {211} crystal planes, and 0.2% proof stress for alloy plates having the components shown in the figure.
The degree of integration of the {211} crystal plane was measured by comparing the relative X-ray diffraction intensity ratio of the (422) diffraction plane of the alloy plate after annealing before pressing with (11).
1), (200), (220), (311), (33)
Relative X of each diffraction surface of 1), (420) and (422)
It was determined by dividing by the sum of the line intensity ratios. Where relative X
The X-ray diffraction intensity ratio is obtained by dividing the X-ray diffraction intensity measured on each diffraction surface by the theoretical X-ray diffraction intensity of the diffraction surface.
For example, the relative X-ray diffraction intensity ratio of the (111) diffraction plane is (11)
1) The X-ray diffraction intensity of the diffraction surface is divided by the theoretical X-ray diffraction intensity of the (111) diffraction surface. The measurement of the degree of integration of the {112} crystal plane is equivalent to the {211} plane in terms of the orientation (42
2) The measurement was performed by measuring the X-ray diffraction intensity of the diffraction surface. As shown in FIG. 1, the 0.2% proof stress is 28.5 kgf / mm ² or less, the degree of integration of the {211} crystal plane is 16% or less, and no cracking of the alloy sheet occurs during press forming. The excellent effects intended in the present invention are exhibited. From the above study results, the degree of integration of the {211} crystal plane was determined to be 16% or less as a condition for suppressing cracking of the alloy sheet.

As described above, the O, B,
With the provisions of Si and N and 0.2% proof stress after annealing before pressing,
The press forming quality intended in the present invention can be improved by the degree of integration and the definition of the {211} crystal plane.

A method for reducing the degree of integration of the {211} crystal plane to 16% or less will be described with reference to FIG. FIG.
Means that the hot-rolled steel strip of the alloy of the present invention is annealed and not annealed, and thereafter, cold-rolled-annealed (890 ° C. × 1 min)
-Finish cold rolling (21%)-Annealing before press (750 ° C x
15 min) shows the degree of integration of the {211} crystal plane of the alloy plate that has passed through the step of 15 min) and the elongation value in a tensile test. When the hot-rolled sheet annealing is performed at 910 to 990 ° C., the degree of integration of the {211} crystal plane is 16% or less. Therefore, in the present invention, the temperature range in hot-rolled sheet annealing is 910 to 990 as a condition for reducing the degree of integration of the {211} crystal plane to 16% or less.
° C.

The hot-rolled sheet annealing in the present invention is exhibited when the hot-rolled steel strip of the present alloy is sufficiently recrystallized before hot-rolled sheet annealing. In order to obtain the degree of {211} crystal plane integration intended in the present invention, slab homogenization heat treatment after slab rolling is not preferable in producing the present alloy. For example, the above-mentioned homogenization heat treatment is performed at
If the treatment is performed for 0 hours or more, the degree of integration of the {211} crystal plane exceeds the specified value of the present invention, and thus such processing must be avoided.

Although the mechanism of cracking of the material at the time of press forming when the degree of integration of the {211} crystal plane exceeds 16% is not necessarily clear, the C direction shown in FIG. In terms of the elongation value in the direction perpendicular to the rolling direction of the {211} crystal plane, when the degree of integration of the {211} crystal plane is high, the value of the elongation shows a low value. It is presumed that, when it becomes high, the value of this elongation decreases, and the fracture limit becomes low, so that cracks may occur.

The 0.2% proof stress after annealing before pressing is 28.5 kgf /, while the degree of integration of the {211} crystal plane is 16% or less.
In order to make it equal to or less than mm ² , in addition to the above-mentioned rules, it is important to control the finish cold elongation, the austenitic crystal grain size before that, and the annealing conditions before pressing.

FIG. 3 shows a tensile test performed on an alloy sheet prepared by manufacturing a hot-rolled steel strip of the alloy of the present invention in the manufacturing process shown in the figure.
The 0.2% proof stress was measured. The annealing after cold rolling changes the temperature to obtain a predetermined austenite crystal grain size.

According to FIG. 3, the finish cold rolling reduction (R%) is 1
6.38D-133.9 ≦ R ≦ 6.3, depending on the austenite grain size (Dμm) before finish cold rolling.
8D-51.0 provides 0.2% proof stress of 28.5 kgf
/ Mm ² or less.

R is less than 16% or 6.38D-1
In the case of 33.9> R, under the annealing conditions before pressing specified in the present invention, the recrystallization is insufficient and the growth of recrystallized grains is also insufficient, so that the 0.2% proof stress is 28%. .5 kgf /
It is more than mm ² and is not suitable. On the other hand, when R exceeds 75% or R> 6.38D-51.0, 100% recrystallization occurs under the annealing conditions before pressing specified in the present invention, but the nucleation frequency during recrystallization becomes too high. Because the crystal grains are fine, 0.2
The% proof stress is more than 28.5 kgf / mm ² and is not suitable.

From the above-mentioned relationship, the 0.2% proof stress is 28.5 kgf / mm ^{2 under the} pre-press annealing conditions characterized by the present invention.
As conditions for obtaining the following, R: 16 to 75%, 6.38
D-133.9 ≦ R ≦ 6.38 D-51.0 was determined. If the appropriate finish cold rolling reduction (R%) and the austenite grain size (Dμm) before the finish cold rolling are within such ranges, the {211} crystal on the alloy plate surface after the pre-press annealing is obtained. The degree of integration of the surface can be 16% or less.

The structure control of the alloy of the present invention as described above
In addition to controlling the texture during hot-rolled sheet annealing, this is achieved by properly controlling the nucleation frequency during recrystallization by combining the crystal grain size before finish cold rolling and the appropriate finish cold-rolling rate according to the combination. It is a thing. By optimizing the combination of D and R described above, 0.1% after annealing before press.
It is possible to lower the 2% proof stress. That is,
R: 21-70%, 6.38D-122.6 ≦ R ≦ 6.38D
By selecting R and D that satisfy the condition of -65.2,
The 0.2% proof stress can be made 28.0 kgf / mm ² or less.

Further, R: 26-63%, 6.38D-10
By selecting R and D satisfying the condition of 8.0 ≦ R ≦ 6.38D−79.3, the 0.2% proof stress can be reduced to 27.5 kgf / mm ² or less. The austenitic crystal grain size before the finish cold rolling intended in the present invention is based on the hot rolled steel strip according to the present invention.
It can be obtained accurately by annealing the hot-rolled sheet under a predetermined condition and then appropriately performing annealing after the subsequent cold rolling at 860 to 950 ° C. for 0.5 to 2 minutes.

In the present invention, while the degree of integration of the {211} crystal plane on the surface of the alloy plate is 16% or less, the 0.2% proof stress after annealing before press is 28.5 kgf / mm ² or less. To do so, it is important to control the annealing conditions before pressing, in addition to the above-mentioned rules. This will be described with reference to FIG. 4. FIG. 4 shows that the components, hot-rolled sheet annealing conditions, austenite crystal grain size before finish cold rolling, and finish cold rolling reduction of the alloy plate within the range of the present invention are obtained. It shows the relationship between the 0.2% proof stress after pre-press annealing and the degree of integration of the {211} crystal plane and the pre-press annealing temperature (T) and time (t).

As is apparent from FIG. 4 as described above,
Hot rolled sheet annealing conditions, even if the austenite crystal grain size and the finish cold rolling rate before finish cold rolling are within the scope of the present invention,
In the case of T <−53.8 log t + 806, recrystallization is not sufficiently performed, the 0.2% proof stress is more than 28.5 kgf / mm ² , and Δ2
The degree of integration of the 11 ° crystal plane is more than 16%, which is not suitable. If T exceeds 790 ° C. or t exceeds 40 min, the {211} crystal plane develops and the degree of integration of this crystal plane exceeds 16%, which is not suitable. From these relationships, the 0.2% proof stress and the ｛2
As conditions for obtaining the degree of integration of the 11 ° crystal plane, T: 720 to
790 ° C., t: 2 to 40 min, T ≧ −53.8 log t + 8
06 was set.

FIG. 5 shows the alloy of the present invention (alloy No. 1).
And comparative alloys (alloys No. 7 and No. 8)
When the alloy plate manufactured by the manufacturing process in the figure is annealed,
It shows changes in the 2% proof stress and the degree of integration of the {211} crystal plane with the annealing time. The hot rolled sheet annealing conditions, the austenite crystal grain size before the finish cold rolling, and the finish cold rolling reduction are within the scope of the present invention.

According to FIG. 5 described above, when the alloy of the present invention is used, the 0.2% proof stress and the {211} crystal plane are obtained within the pre-press annealing conditions within the range of the present invention shown in FIG. Is within the range specified by the present invention. On the other hand, in the case of the comparative alloy, even at the time of annealing at 750 ° C., 0.2%
The yield strength is more than 28.5 kgf / mm ² , and the degree of integration of the {211} crystal plane is more than the specified value of the present invention, and it is clear that there is a problem in press formability. Thus, in the present invention, it is understood that the composition of the alloy is extremely important in addition to the definition of the manufacturing method.

Further, the annealing before press forming in the present invention may be performed before the photoetching. In this case, if the annealing conditions before press forming are within the provisions of the present invention,
The required photo-etching quality can be ensured.

The alloy thin plate after annealing before press was # 2
Methods for controlling the degree of integration of the 11｝ crystal plane within the range specified in the present invention include, in addition to the above-mentioned methods, adoption of rapid solidification, texture control by controlling recrystallization in hot working, and the like.

[0062]

The present invention as described above will be described in more detail with reference to specific examples as follows. (Example 1) Steel ingots composed of alloys No. 1 to No. 18 having the chemical components shown in the following Tables 1 and 2 were prepared by ladle refining.

[0063]

[Table 1]

[0064]

[Table 2]

Each of the ingots in Tables 1 and 2 as described above was prepared by subjecting each of the ingots to bulk rolling, surface flaw removal, hot rolling (heating at 1100 ° C. × 3 hours). Thereafter, hot-rolled sheet annealing (930 ° C.)-Cold rolling-annealing (conditions shown in Table 3) -finishing cold rolling (21% reduction) were performed to obtain an alloy sheet having a sheet thickness of 0.25 mm. . These hot rolled steel strips were sufficiently recrystallized after hot rolling. After these alloy plates were made into flat masks by etching, the flat masks were subjected to pre-press annealing under the condition of 750 ° C. × 15 min, and then subjected to press forming to obtain a shape freezing property, conformity with a mold, and material. The occurrence of cracks was examined according to the evaluation criteria shown in Tables 1 and 2 (alloys No. 1 to No. 18
Material Nos. 1 to 18). Tensile properties (0.2% proof stress and elongation in the direction perpendicular to the rolling direction) and the degree of integration of {211} crystal planes were examined after annealing before pressing. Tensile properties are measured at room temperature. The degree of integration of the {211} crystal plane was measured by the above-mentioned X-ray diffraction.

[0066]

[Table 3]

As is evident from the results shown in Tables 1 and 2, it has a component composition within the scope of the present invention, and has a {211} crystal plane density and 0.2% within the scope of the present invention. Each of the materials No. 1 to No. 13 having a proof stress has an excellent level of press forming quality.

On the other hand, materials No. 14 and No. 1
Each of the materials No. 6 is a case where the amounts of Si and N exceed the requirements of the present invention, and there is a problem in that the materials are compatible with the mold. material
No. 15 is a case where the amount of O exceeds the regulation of the present invention.
% Proof stress is poor shape fixability in exceeding 28.5 kgf / mm ^2, it is clear that there is a problem because even occurring cracking of alloy sheet for press molding quality. No. 17 and
Each material of No. 18 was the case where only the B content, the B content and the O content exceeded the stipulation of the present invention, and the 0.2% proof stress was 28.5 k.
It is more than gf / mm ² , and the shape freezing property is inferior. Further, the degree of integration of the {211} crystal planes of these comparative alloys exceeds the value specified in the present invention, and cracks of the alloy plate occur, which is problematic in press forming quality.

As is apparent from the above description, the component composition within the scope of the present invention and the ｛21 within the scope of the present invention
It is clear that by setting the degree of integration of the 1｝ crystal plane and 0.2% proof stress, it is possible to obtain an Fe—Ni-based alloy thin plate for a shadow mask having an excellent level of press molding quality intended in the present invention.

(Example 2) Using the hot-rolled steel strip of alloy No. 1 used in Example 1 described above, hot-rolled sheet annealing was performed under the conditions shown in Table 4 below, and not performed. About cold rolling,
Annealing (890 ° C × 1 min)-Finish cold rolling (Rolling rate 21
%) To obtain an alloy plate having a thickness of 0.25 mm.

[0071]

[Table 4]

After each alloy plate as described above was made into a flat mask by etching, the flat mask was heated to 750 ° C.
Annealed before pressing under the conditions of × 15 min.
~ No. 23 was obtained. Next, press molding is performed. The press molding quality shown in Table 3 was examined. The measuring method of each characteristic value in Table 3 is the same as in Example 1.

As is evident from the results shown in Table 4 above, the component composition within the scope of the present invention, the degree of integration of the {211} crystal plane, the 0.2% proof stress, and the finish cold finish within the scope of the present invention. It has the austenitic grain size before rolling, the finish cold rolling reduction and the pre-press annealing conditions, and the hot-rolled sheet annealing conditions are also within the range of the present invention. The quality shows an excellent level.

On the other hand, the materials No. 21 to No. 23 each have a hot-rolled sheet annealing temperature lower than the lower limit specified in the present invention, higher than the upper limit, and one not subjected to the hot-rolled sheet annealing. However, in any of the materials, the degree of integration of the {211} crystal plane exceeds the upper limit specified in the present invention, and cracks of the alloy plate during press forming have occurred. Furthermore, material No.2
In No. 3, the 0.2% proof stress is more than 28.5 kgf / mm ² , and there is a problem in the shape freezing property during press molding.

As described above, it is understood that it is important to make the hot-rolled sheet annealing within the range of the present invention in order to keep the degree of integration of the {211} crystal plane within the range of the present invention.

(Example 3) Alloys No. 1, No. 2, No. 4, and No. 1 used in Example 1
Using hot-rolled steel strips No. 6, No. 7, No. 9, No. 11, No. 12, No. 13 and No. 8, subsequent hot-rolled sheet annealing (93
0 ° C)-Cold rolling-Annealing (implemented by holding at the temperature shown in Table 4 for 1 min) Finish cold rolling (implemented at the rolling reduction shown in Table 3) to obtain a 0.25 mm thick alloy sheet I got
After turning these alloy plates into flat masks by etching, the flat masks were annealed before pressing under the conditions of 750 ° C. × 15 min to obtain materials No. 24 to No. 61. Next, press molding was performed, and the press molding quality shown in the following Tables 5 and 6 was examined. The measuring method of each characteristic value in Table 4 is the same as in Example 1.

[0077]

[Table 5]

[0078]

[Table 6]

As is evident from the results shown in Tables 5 and 6, the austenite grains before the finish cold rolling were obtained even when the component composition, the hot-rolled sheet annealing conditions and the pre-press annealing conditions were within the scope of the present invention. Material No. 25 to No. 30, No. 33, whose diameter and finish cold rolling ratio are within the range specified by the present invention.
Each of the materials No. 36 to No. 38 and No. 42 to No. 61 has a {211} crystal plane integration degree of 16% or less, and particularly the materials No. 25, No. 30, No. 33, And No.3
6, No.42, No.44, No.45, No.49, No.5
No. 5, No. 58 and No. 61 are within the range of the area 1 specified in the present invention, and the 0.2% proof stress is 28.5 kgf / mm ² or less, and the materials No. 26, No. 28 and No. .29, No.43, No.4
Nos. 7, No. 50, No. 54, No. 60 and No. 38 are within the range 2 defined in the present invention, and the 0.2% proof stress is 28.0 kgf / mm ² or less. .27, No.46, No.
No.48, No.51, No.52, No.53, No.56, No.
Each of Nos. 57, No. 59 and No. 37 is within the range of the region 3 specified in the present invention, and the 0.2% proof stress is 27.5 kgf / mm ² or less, which is 0.2% intended in the present invention. The yield strength has been obtained, and all of these materials show excellent levels of press formability. Further, as described above, it can be understood that the shape freezing property can be set to a more excellent level by decreasing the proof stress by 0.2%.

On the other hand, materials No. 24, No. 31,
No.32, No.34, No.35, No.39 and No.4
In each of the materials of No. 0, one or both of the austenite grain size before the finish cold rolling and the finish cold rolling ratio are out of the range specified in the present invention, the 0.2% proof stress and / or {211}
The degree of integration of crystal planes exceeds the stipulations of the present invention, and there is a problem in press forming at least one of shape freezing and cracking of the alloy sheet.

Material No. 41 was obtained under the condition of annealing at 850 ° C. for 1 minute before the finish cold rolling. In such annealing, the austenite grain size was 10.0 μm.
Even when the subsequent finish cold rolling reduction is 15%, it is 0.2%.
The% proof stress is more than 28.5 kgf / mm ² , and the shape freezing property at the time of press molding intended in the present invention has not been obtained.

As described above, even in the case of the component composition, hot-rolled sheet annealing conditions and pre-press annealing conditions within the scope of the present invention, the austenite grain size and the finish cold rolling ratio before the finish cold rolling are within the scope of the present invention. It is understood that it is necessary to obtain the press forming quality intended in the present invention.

(Example 4) Alloys No. 1, No. 4, No. 17, No. 1 used in Example 1
Using hot-rolled steel strips No. 18, No. 9, No. 10 and No. 12, thereafter hot-rolled sheet annealing (930 ° C.)-Cold rolling-annealing (890 ° C. × 1 min) -finish cold rolling (reduction) Rate 21%)
Was performed to obtain an alloy plate having a plate thickness of 0.25 mm. After these alloy plates were made into flat masks by etching, the flat masks were annealed before pressing under the conditions shown in Table 7 below, and N
o. Materials of 62-79 were obtained. Then, press molding was performed, and the press molding quality shown in Table 7 was examined. The measuring method of each characteristic value in Table 7 is the same as that in Example 1.

[0084]

[Table 7]

As is clear from the results shown in Table 7, even in the case of the component composition, the hot rolling conditions, the austenite grain size before the finish cold rolling and the finish cold rolling reduction within the range of the present invention, the Each of the materials No. 62, No. 64, No. 71 to No. 79 and No. 65 whose annealing conditions (temperature and time) are within the range of the present invention has a {211} crystal plane density of 16 % Or less, and the 0.2% proof stress is also within the range of the present invention, and all the materials show excellent press forming quality.

On the other hand, materials No. 66, No. 67,
And No. 68, the pre-press annealing temperature was lower than the lower limit, higher than the upper limit, and higher than the upper limit, and the time exceeded the upper limit. Exceeding, and cracking of the alloy has occurred. In addition, the temperature of the material No. 66 is lower than the lower limit, and the 0.2% proof stress is 28.5 kgf / mm ² .

Material No. 63 has a conditional expression (T ≧ −53.T) consisting of temperature (T) and time (t) in annealing before pressing.
8 log t + 806) are those which do not satisfy the, there is a 0.2% proof stress is a problem with shape fixability at the time of press-molding at 28.5 kgf / mm ^2, greater than {211} crystal plane of integration even at 16 percent Thus, cracking of the alloy plate during press forming has also occurred.

The materials No. 69 and No. 70 used the comparative alloys. However, even when the pre-press annealing was performed at 750 ° C. for 60 minutes, the 0.2% proof stress was not exceeded. More than 28.5 kgf / mm ² , there is a problem in shape freezing during press molding. In these materials, {211}
The degree of integration of crystal planes is more than 16%, and cracks of the alloy plate during press forming have also occurred.

As described above, even in the case of the component composition, the hot-rolled sheet annealing conditions, the austenite grain size before finish cold rolling and the finish cold rolling reduction within the scope of the present invention, the annealing conditions before pressing are determined by the present invention. It is understood that it is necessary to be within the range in order to obtain the press forming quality intended in the present invention.

(Example 5) Using the hot-rolled steel strips of alloys No. 1 and No. 4 used in the example, thereafter, hot-rolled sheet annealing (930 ° C.)-Cold rolling-annealing (8
90 ° C. × 1 min) -finish cold rolling (rolling reduction 21%) was performed to obtain an alloy plate having a thickness of 0.25 mm. These alloy sheets were annealed before press under the conditions shown in Table 8 below, No. 80 to No. 8
Material 2 was obtained. After forming a flat mask by subsequent etching, press molding was performed, and the press molding quality shown in Table 6 was examined. The measuring method of each characteristic value in Table 8 is the same as in Example 1. The etching property was examined by visually observing the state of occurrence of unevenness in the flat mask after etching.

[0091]

[Table 8]

As is clear from the results shown in Table 8, the component composition, hot rolling conditions, austenite grain size before finish cold rolling, finish cold rolling reduction, and annealing conditions before press within the scope of the present invention were obtained. Material Nos. 80 to No.
Each of the materials No. 82 had good etching properties without any unevenness, and had a degree of integration of {211} crystal planes of 16% or less, and a 0.2% proof stress was within the specification of the present invention. It shows excellent press forming quality.

As described above, the component composition, hot-rolled sheet annealing conditions, austenite grain size of the finish cold-rolled surface, finish cold-rolling reduction, and annealing conditions before pressing within the scope of the present invention are within the scope of the present invention. It is necessary to obtain the press forming quality intended in the present invention, and after annealing before pressing,
Even when the etching is performed, it is understood that the obtained flat mask has no unevenness and the required etching property can be obtained.

As apparent from Examples 1 to 5 described above, when the degree of integration of the {211} crystal plane is more than 16%, the elongation in the direction perpendicular to the rolling direction after the pre-press annealing is less than that of the present invention. If the degree of integration of the {211} crystal plane is high compared to the example,
It is presumed that this elongation value decreases and cracks occur during press molding.

(Example 6) Next, Ni: 35.7%, Si: 0.01%, O: 0.0014
%, N: 0.015%, B: 0.0001%, C: 0.050
%, Mn: 0.34%, Cr: 0.04%, balance substantially from Fe
Fe-Ni alloy is cast directly on a thin cast plate, and this thin cast plate is
At a temperature of 300 to 1000 ° C and a rolling reduction of 30% or less
After hot working, it was wound at 800 ° C. to obtain a hot rolled sheet. This
After that, using the hot rolled steel strip of
Table 9 below shows the results
It is shown.

[0096]

[Table 9]

As is clear from the results shown in Table 9 above.
In addition, the component composition within the scope of the present invention, hot rolling conditions, finishing cold
Austenitic grain size before rolling, finish cold rolling reduction and
Material No. 83- whose annealing conditions before press are within the range of the present invention
85 each material has good etching properties without unevenness
And the degree of integration of the {211} crystal plane is 16% or less.
The 0.2% proof stress is also within the scope of the present invention.
It shows excellent press forming quality.

Example 7 N: 35.7%, Si: 0.01%, O: 0.0014
%, N: 0.0015%, B: 0.0001%, C: 0.00
50%, Mn: 0.34%, Cr: 0.04%, balance substantially Fe
Obtained by directly casting an Fe-Ni alloy consisting of
Annealing (930 ° C)-Cold Rolling-Annealing (890 ° C x
1 min)-Finish cold rolling (21% reduction). Board
An alloy plate having a thickness of 0.25 mm was obtained. With subsequent etching
After flat masking, these alloys are listed in Table 10 below.
Annealed before pressing under the conditions shown to obtain materials No. 86 to 88
Was. Thereafter, press molding is performed. Press molding shown in Table 6
Checked the quality. The measuring method of each characteristic value in Table 10 is an example.
Same as 1.

[0099]

[Table 10]

As is clear from the results shown in Table 10 above.
In addition, the component composition within the scope of the present invention, hot rolling conditions, finishing cold pressure
Austenite grain size before finishing, cold rolling reduction,
No. 86-88 whose pre-annealing conditions are within the range of the present invention
Each of the materials has good etching properties without unevenness
The degree of integration of the {211} crystal plane is 16% or less,
The 2% proof stress is also within the range of the present invention, and all materials are excellent.
Shows the press forming quality.

As described above, the component set within the scope of the present invention
Austenite before cold rolling
The grain size, finish cold rolling rate and annealing conditions before pressing
Press-formed product intended in the present invention to be within the scope of the invention
Necessary to get the quality.

[0102]

According to the present invention as described in detail above,
Excellent press formability and annealing before press at 720 ° C to 7 ° C
The required press-forming quality even at a low annealing temperature of 90 ° C and a short annealing time of 40 min or less, that is, excellent shape freezing property at the time of molding, good compatibility with molds and suppression of cracking of materials. The present invention can provide an Fe-Ni-based Invar alloy thin plate for a shadow mask and a method for producing the same, which can provide the following effects.

Furthermore, according to the present invention, even if annealing before press forming is performed before etching, required etching quality and press forming quality can be obtained. Since the present invention can provide an Fe-Ni-based invar alloy thin plate for a shadow mask, which is capable of producing such a shadow mask, an industrially advantageous effect is brought about, and the invention has a great effect.

[Brief description of the drawings]

FIG. 1 is a table showing the relationship between the occurrence of cracks during press forming, the degree of integration of {211} crystal planes, and the 0.2% proof stress after pre-press annealing.

FIG. 2 is a table showing the relationship between the degree of integration of {211} crystal planes, elongation in the direction perpendicular to rolling, and the hot-rolled sheet annealing temperature.

FIG. 3 is a table showing a relationship between 0.2% proof stress after pre-press annealing, austenite crystal grain size before finish cold rolling, and finish cold rolling reduction.

FIG. 4 is a table showing the relationship between 0.2% proof stress after pre-press annealing, the degree of integration of {211} crystal planes, and pre-press annealing conditions.

FIG. 5 is a table showing the relationship between 0.2% proof stress after pre-press annealing, the degree of integration of {211} crystal planes, and pre-press annealing conditions.

Continuation of front page (56) References JP-A-4-341543 (JP, A) (58) Fields investigated (Int. Cl. ⁷ , DB name) C21D 9/46 C21D 8/02 C22C 38/00 302 H01J 29/07

Claims (19)

(57) [Claims] (1) Ni content: 34-38% in wt%, S:
i: 0.05% or less, B: 0.0005% or less, O: 0.002
0% or less, N: 0.0015% or less, hot-rolled steel strip of low thermal expansion alloy, hot-rolled sheet annealing, then cold rolling and subsequent recrystallization annealing, and then finish cold rolling In producing in the application step, the hot-rolled sheet annealing is performed at 910 to 990 ° C., and the reduction (R)% in the finish cold rolling is determined according to the austenite grain size D (μm) after the recrystallization annealing. Annealing is performed within the range of the region I shown in FIG.
By applying under the condition of ４０40 min and T ≧ −53.8 logt + 806, 0.2% in the alloy plate after annealing is obtained.
A method for producing an Fe-Ni alloy sheet for a shadow mask excellent in press formability, wherein the proof stress is adjusted to 28.5 kgf / mm ² or less and the degree of integration of {211} crystal faces is adjusted to 16% or less. 2. A hot-rolled steel strip of a low-thermal-expansion alloy having the component described in claim 1 is subjected to hot-rolled sheet annealing, and then to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing by hot rolling, the hot rolled sheet annealing is performed at 910
Degree of reduction (R%) in cold rolling at finish
Is the austenite grain size D (μ)
m) is performed within the range of the region II shown in FIG. 3, and the subsequent annealing before press forming is performed at a temperature (T ° C.) of 720 to 79 ° C.
0 ° C., time (tmin) is 2 to 40 min and T ≧ −53.8 lo
By applying under conditions satisfying gt + 806, the 0.2% proof stress of the annealed alloy plate is adjusted to 28.0 kgf / mm ² or less, and the degree of integration of {211} crystal planes is adjusted to 16% or less. For shadow masks with excellent press moldability
Manufacturing method of Fe-Ni alloy sheet. 3. A hot-rolled steel strip of a low-thermal-expansion alloy having the component according to claim 1 is subjected to hot-rolled sheet annealing, and then to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing in the process of applying, the hot rolled sheet annealing is performed at 910 ° C.
~ 990 ° C, reduction rate in finish cold rolling (R%)
Is the austenite grain size D (μ)
m) within the range shown in the area III shown in FIG.
Subsequently, the temperature (T ° C.) of the annealing before press forming is 720.
７790 ° C., time (tmin) is 2-40 min and T ≧ −5
By applying under the condition that satisfies 3.8 log t + 806,
A shadow mask excellent in press formability, characterized in that the 0.2% proof stress of the alloy plate after annealing is adjusted to 27.5 kgf / mm ² or less and the degree of integration of {211} crystal faces is adjusted to 16% or less. Of manufacturing Fe-Ni alloy sheet for use. 4. A hot-rolled steel strip of a low-thermal-expansion alloy having the composition described in claim 1 is subjected to hot-rolled sheet annealing, and then to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When producing in the step of applying, the hot-rolled sheet annealing is performed at 910 to 990 ° C.
The rolling reduction (R)% in the finish cold rolling is performed within the range of the region I shown in FIG. 3 in accordance with the austenite grain size D (μm) after the above-mentioned recrystallization annealing. In the previous annealing, the temperature (T ° C.) is 720 to 790 ° C., the time (tmin) is 2 to 40 min, and T ≧ −53.8 logt + 8.
06, the 0.2% proof stress of the annealed alloy sheet is 28.5 kgf / mm ² or less, and
Fe-Ni for shadow masks excellent in press formability, characterized in that the degree of integration of 11 ° crystal planes is adjusted to 16% or less.
Manufacturing method of alloy sheet. 5. A hot-rolled steel strip of a low-thermal-expansion alloy having the component described in claim 1 is subjected to hot-rolled sheet annealing, then to cold rolling and subsequent recrystallization annealing, and then to finish cold rolling. When manufacturing in the process of applying, the hot rolled sheet annealing is performed at 910 ° C.
~ 990 ° C, reduction rate in finish cold rolling (R%)
Is the austenite grain size D (μ)
m) is performed within the range of the region II shown in FIG.
７790 ° C., time (tmin) is 2-40 min and T ≧ −5
By applying under conditions that satisfy 3.8 logt + 806,
A shadow mask excellent in press formability, characterized in that the alloy plate after annealing has a 0.2% proof stress of 28.0 kgf / mm ² or less and the degree of integration of {211} crystal faces is adjusted to 16% or less. Of manufacturing Fe-Ni alloy sheet for use. 6. A hot-rolled steel strip of a low-thermal-expansion alloy having the component according to claim 1 is subjected to hot-rolled sheet annealing, and then to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing in the process of applying, the hot rolled sheet annealing is performed at 910 ° C.
~ 990 ° C, reduction rate in finish cold rolling (R%)
Is the austenite grain size D (μ)
m) within the range shown in the area III shown in FIG.
The temperature (T ° C.) of the annealing before the press forming after the etching process is 720 to 790 ° C., and the time (tmin) is 2 to 40 min and T
By applying under the condition that ≧ −53.8 log t + 806, the 0.2% proof stress of the annealed alloy sheet is 27.5 kgf / m.
A method for producing an Fe—Ni alloy sheet for a shadow mask having excellent press formability, wherein the degree of integration of {211} crystal planes is adjusted to 16% or less and m ² or less. 7. A hot-rolled steel strip of a low-thermal-expansion alloy having the composition described in claim 1 is subjected to hot-rolled sheet annealing, and then to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When producing in the step of applying, the hot-rolled sheet annealing is performed at 910 to 990 ° C.
The rolling reduction (R)% in the finish cold rolling is performed within the range of the region I shown in FIG. 3 according to the austenite grain size D (μm) after the above-mentioned recrystallization annealing. Annealing time (T ° C) 720-790 ° C, time (tmin)
Is applied for 2 to 40 min and under the condition of T ≧ −53.8 log + 806 to obtain 0.1% in the alloy plate after annealing.
Fe for a shadow mask excellent in press formability, characterized in that a 2% proof stress is adjusted to 28.5 kgf / mm ² or less, and the degree of integration of {211} crystal planes is adjusted to 16% or less and then etched. -Manufacturing method of Ni alloy sheet. 8. A hot-rolled steel strip of a low-thermal-expansion alloy having the component according to claim 1 is subjected to hot-rolled sheet annealing, then to cold rolling and subsequent recrystallization annealing, and then to finish cold rolling. When manufacturing in the process of applying, the hot rolled sheet annealing is performed at 910 ° C.
~ 990 ° C, reduction rate in finish cold rolling (R%)
Is the austenite grain size D (μ)
m) is performed within the range of the region II shown in FIG. 3, and the subsequent annealing before press forming is performed at a temperature (T ° C.) of 720 to 79 ° C.
0 ° C., time (tmin) is 2 to 40 min and T ≧ −53.8 log
By applying under the condition satisfying t + 806, the 0.2% proof stress of the alloy plate after annealing is adjusted to 28.0 kgf / mm ² or less and the degree of integration of the {211} crystal plane is adjusted to 16% or less.
A method for producing a Fe—Ni alloy thin plate for a shadow mask having excellent press formability, characterized by performing etching. 9. A hot-rolled steel strip of a low-thermal-expansion alloy having the component described in claim 1 is subjected to hot-rolled sheet annealing, and then to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing in the process of applying, the hot rolled sheet annealing is performed at 910 ° C.
~ 990 ° C, reduction rate in finish cold rolling (R%)
Is the austenite grain size D (μ)
m) within the range shown in the area III shown in FIG.
Subsequently, the temperature (T ° C.) of the annealing before press forming is 720.
７790 ° C., time (tmin) is 2-40 min and T ≧ −5
By applying under the condition that satisfies 3.8 log t + 806,
Press forming characterized by adjusting the 0.2% proof stress of the annealed alloy plate to 27.5 kgf / mm ² or less and adjusting the degree of integration of {211} crystal planes to 16% or less, and then performing etching. Method for producing Fe-Ni alloy thin plate for shadow mask with excellent resistance. 10. A low-thermal-expansion alloy having the composition described in claim 1 is cast directly into a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing in the step of applying, annealing of the thin cast plate is performed at 910 to 9
The rolling was performed at 90 ° C., and the rolling reduction (R)% in the finish cold rolling was performed within the range of the region I shown in FIG. 3 in accordance with the austenite grain size D (μm) after the recrystallization annealing described above. The temperature (T ° C.) of the annealing before forming is 720 to 790 ° C., the time (tmin) is 2 to 40 min, and T ≧ −53.8 logt + 80.
6, the 0.2% proof stress of the annealed alloy sheet is 28.5 kgf / mm ² or less, and
1) A method for producing an Fe-Ni alloy sheet for a shadow mask excellent in press formability, wherein the degree of integration of crystal planes is adjusted to 16% or less. 11. A low-thermal-expansion alloy having the component described in claim 1 is cast directly into a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing in a process, the annealing of the thin cast
It is applied at 10 ° C. to 990 ° C., and the rolling reduction (R
%) Is the austenite grain size D after the recrystallization annealing described above.
(Μm) in the range of the region II shown in FIG. 3 and the subsequent annealing before press forming is performed at a temperature (T ° C.) of 720 to
790 ° C., time (tmin) is 2 to 40 min, and T ≧ −53.
By applying it under the condition satisfying 8 logt + 806, the 0.2% proof stress of the annealed alloy plate is adjusted to 28.0 kgf / mm ² or less and the degree of integration of the {211} crystal plane is adjusted to 16% or less. Method for producing Fe-Ni alloy sheet for shadow mask with excellent press formability. 12. A low-thermal-expansion alloy having the composition described in claim 1 is cast directly into a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing in a process, the annealing of the thin cast
It is applied at 10 ° C. to 990 ° C., and the rolling reduction (R
%) Is the austenite grain size D after the recrystallization annealing described above.
(Μm) according to the range III shown in FIG. 3 and the subsequent annealing before press forming is performed at a temperature (T ° C.) of 7 ° C.
20 to 790 ° C, time (tmin) is 2 to 40 min and T ≧
By applying the condition satisfying −53.8 log t + 806, the 0.2% proof stress of the annealed alloy sheet is 27.5 kgf / mm ^2.
A method for producing an Fe—Ni alloy sheet for a shadow mask having excellent press formability, wherein the degree of integration of {211} crystal planes is adjusted to 16% or less. 13. A low-thermal-expansion alloy having the composition described in claim 1 is cast directly into a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing in the step of applying, annealing of the thin cast plate is performed at 910 to 9
The reduction rate (R)% in the finish cold rolling is performed within the range of the region I shown in FIG. 3 according to the austenite grain size D (μm) after the recrystallization annealing. The temperature (T ° C.) of the annealing before press forming is 720 to 790.
° C, time (tmin) is 2 to 40 min and T ≧ -53.8 logt
By applying it under the condition satisfying +806, the 0.2% proof stress of the alloy plate after annealing is adjusted to 28.5 kgf / mm ² or less, and the degree of integration of the {211} crystal plane is adjusted to 16% or less. Fe for shadow mask with excellent press moldability
-Manufacturing method of Ni alloy sheet. 14. A low-thermal-expansion alloy having the component described in claim 1 is cast directly into a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing in a process, the annealing of the thin cast
It is applied at 10 ° C. to 990 ° C., and the rolling reduction (R
%) Is the austenite grain size D after the recrystallization annealing described above.
(Μm) in accordance with the range of the region II shown in FIG.
20 to 790 ° C, time (tmin) is 2 to 40 min and T ≧
By applying the condition satisfying −53.8 logt + 806, the 0.2% proof stress of the alloy plate after annealing is 28.0 kgf / mm ^2.
A method for producing an Fe—Ni alloy sheet for a shadow mask having excellent press formability, wherein the degree of integration of {211} crystal planes is adjusted to 16% or less. 15. A low-thermal-expansion alloy having the component described in claim 1 is cast directly into a thin cast plate, annealed, cold-rolled, and subsequently recrystallization-annealed, and then subjected to finish cold-rolling. When manufacturing in a process, the annealing of the thin cast
It is applied at 10 ° C. to 990 ° C., and the rolling reduction (R
%) Is the austenite grain size D after the recrystallization annealing described above.
(Μm) within the range shown in the region III shown in FIG.
° C) is 720 to 790 ° C, and the time (tmin) is 2 to 40 min.
In addition, by applying under the condition that T ≧ −53.8 log t + 806, the 0.2% proof stress of the annealed alloy sheet is 27.5.
kgf / mm ² or less and the degree of integration of {211} crystal plane is 16
%. A method for producing an Fe—Ni alloy thin plate for a shadow mask, which is excellent in press formability, and is adjusted to be equal to or less than 0.1%. 16. A low thermal expansion alloy having the composition described in claim 1 is cast directly into a thin cast plate, annealed, and then subjected to cold rolling and subsequent recrystallization annealing, followed by finish cold rolling. When manufacturing in the step of applying, annealing of the thin cast plate is performed at 910 to 9
The rolling was performed at 90 ° C., and the rolling reduction (R)% in the finish cold rolling was performed within the range of the region I shown in FIG. 3 in accordance with the austenite grain size D (μm) after the recrystallization annealing described above. The temperature (T ° C.) of the annealing before forming is 720 to 790 ° C., the time (tmin) is 2 to 40 min, and T ≧ −53.8 logt + 80.
6, the 0.2% proof stress of the annealed alloy sheet is 28.5 kgf / mm ² or less, and
1) A method for producing an Fe-Ni alloy thin plate for a shadow mask excellent in press formability, wherein etching is performed after adjusting the degree of integration of crystal planes to 16% or less. 17. A low-thermal-expansion alloy having the component according to claim 1 is cast directly into a thin cast plate, annealed, cold-rolled, and subsequently recrystallization-annealed, and then subjected to finish cold-rolling. When manufacturing in a process, the annealing of the thin cast
It is applied at 10 ° C. to 990 ° C., and the rolling reduction (R
%) Is the austenite grain size D after the recrystallization annealing described above.
(Μm) in the range of the region II shown in FIG. 3 and the subsequent annealing before press forming is performed at a temperature (T ° C.) of 720 to
790 ° C., time (tmin) is 2 to 40 min, and T ≧ −53.
Etching after adjusting the alloy plate after annealing to have a 0.2% proof stress of 28.0 kgf / mm ² or less and a {211} crystal plane integration degree of 16% or less by applying a condition satisfying 8 logt + 806. A method for producing an Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability, characterized by performing the following. 18. A low-thermal-expansion alloy having the component according to claim 1 is cast directly into a thin cast plate, annealed, cold-rolled, and subsequently recrystallization-annealed, and then subjected to finish cold-rolling. When manufacturing in a process, the annealing of the thin cast
It is applied at 10 ° C. to 990 ° C., and the rolling reduction (R
%) Is the austenite grain size D after the recrystallization annealing described above.
(Μm) according to the range III shown in FIG. 3 and the subsequent annealing before press forming is performed at a temperature (T ° C.) of 7 ° C.
20 to 790 ° C, time (tmin) is 2 to 40 min and T ≧
By applying the condition satisfying −53.8 log t + 806, the 0.2% proof stress of the annealed alloy sheet is 27.5 kgf / mm ^2.
A method for producing a Fe-Ni alloy thin plate for a shadow mask excellent in press formability, wherein etching is performed after adjusting the degree of integration of {211} crystal planes to 16% or less. 19. Ni content: 34-38% in wt%;
Si: 0.05% or less, B: 0.000001 to 0.0001%,
O: 0.0020% or less, N: 0.0015% or less, C: 0.000%
Fe-Ni alloy containing 0050% or less, Mn: 0.35% or less, Cr: 0.05% or less, and the balance of unavoidable impurities and the composition of Fe. 0.2% proof stress is at 28.5kgf / mm ² or less,
And a shadow mask F excellent in press moldability, characterized in that the degree of integration of the {221} crystal plane is 15% or less.
e-Ni alloy thin plate.