JP3367147B2 - Fe-Ni-based alloy thin plate and Fe-Ni-Co-based alloy thin plate for shadow mask having excellent press formability and method for producing the same - Google Patents

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a Fe-Ni alloy thin plate for a shadow mask having excellent press formability and Fe-.
The present invention relates to a Ni-Co alloy thin plate and a manufacturing method thereof.

2. Description of the Related Art In recent years, with the increasing quality of color televisions,
As a shadow mask alloy capable of coping with the problem of color shift, a Fe-Ni alloy containing 34 to 38 wt% Ni is used. This Fe-Ni alloy has a remarkably small coefficient of thermal expansion as compared with the low carbon steel conventionally used as a shadow mask material. Therefore, Fe-Ni
A shadow mask made of a system alloy is unlikely to cause a problem of color shift due to thermal expansion even when heated by an electron beam.

Usually, an alloy thin plate for a shadow mask is manufactured by subjecting an alloy ingot obtained by a continuous casting method or an ingot making method to slab rolling, hot rolling and cold rolling / annealing. Moreover, the alloy thin plate for a shadow mask manufactured in this way is usually processed into a shadow mask by the following steps. That is, electron beam passage holes are formed by photoetching in a shadow mask alloy thin plate (hereinafter, the shadow mask alloy thin plate that has been punched by this etching is referred to as a "flat mask"), and this flat mask is annealed. After that, it is press-formed into a curved shape so as to match the shape of the cathode ray tube, and then this is assembled into a shadow mask, and the surface thereof is subjected to blackening treatment.

Conventionally, a shadow mask material produced by cold rolling, recrystallization annealing, or recrystallization annealing followed by a slight finish rolling of an Fe-Ni alloy is less than a shadow mask material of low carbon steel. Since the strength is high, 80% before press forming to ensure press formability after etching perforation
Softening annealing (pre-press annealing) at a temperature of 0 ° C or higher,
By making the crystal grains coarse, the softening is aimed at.
Then, spherical molding is performed by a method of warm pressing after the softening annealing. However, the softening
Performing at a temperature as high as 0 ° C or higher is disadvantageous in terms of work efficiency and economy, and it is desired to develop a material that can obtain the same low strength as the material softened and annealed at 800 ° C or higher by the softening and annealing at a lower temperature. There is. Japanese Unexamined Patent Publication (Kokai) No. 3-267320 has been proposed as a technique to meet such a demand. This technique requires 5 to 5 days after cold rolling and subsequent recrystallization annealing.
By performing the finish cold rolling at a rolling rate of 20%,
Press-molding by softening annealing at less than 800 ° C., specifically, 703 ° C. × 60 minutes to obtain 0.2% proof stress at 200 ° C. of 9.5 kgf / mm ² (10 kgf / mm ² or less). It is intended to reduce the strength to a good level.

[0004]

However, even this prior art cannot be said to sufficiently satisfy good warm press formability. That is, the shadow mask material obtained by this prior art has a drawback that galling occurs in the mold during press molding and cracks are likely to occur at the end of the material. Despite these problems, CRT manufacturers have also attempted to shorten the annealing time of softening annealing at the above-mentioned temperature in order to further pursue work efficiency and economic efficiency. Incidentally, the annealing time in this case is 40 minutes or less, and depending on the case, a short time treatment such as 2 minutes may be possible. However, when such an annealing condition is applied to the above-mentioned prior art, the occurrence of galling on the mold during press molding becomes more significant, resulting in frequent cracking of the material, which is a serious quality problem.

In view of such conventional problems, the present invention provides excellent press formability even when softening annealing before press forming is carried out at a temperature as low as 790 ° C. or less and a short time of 40 minutes or less. Fe-Ni for shadow mask
An object is to provide a system alloy thin plate, a Fe-Ni-Co system alloy thin plate, and a method for producing the same. Here, the excellent press moldability in the present invention is excellent in shape fixability at the time of molding, is well compatible with the mold (no galling with the mold),
Moreover, it means that the material does not crack.

[0006]

The inventors of the present invention have conducted extensive studies to develop an Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability. % Press yield and excellent press formability can be obtained by adjusting the degree of integration of {211} crystal planes within a specific range, and a method for producing such an alloy thin plate is Along with hot-rolled sheet annealing, the rolling ratio in finish cold rolling is appropriately controlled according to the average austenite crystal grain size before finish cold rolling, and softening annealing before press forming is performed under predetermined conditions. According to the above, it was found that the 0.2% proof stress and the degree of accumulation of {211} crystal faces of the alloy sheet after softening annealing before press forming can be adjusted within a specific range. The present invention has been made on the basis of such knowledge, and the characteristic configuration is as follows.

[0007]

(1) Ni: 34 to 38 wt%, Si:
0.07 wt% or less, B: 0.0020 wt% or less,
O: 0.0020 wt% or less, N: 0.0020 wt%
Less than, Cr: 0.001 to 0.05 wt%, Co: 1w
t% or less, the balance Fe and unavoidable impurities, 0.2% proof stress after performing softening annealing before press molding is 28.0 kgf / mm ² or less, and the degree of integration of {211} crystal faces on the plate surface is A Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability and is 16% or less.

(2) Ni: 28 to 38 wt%, Si:
0.07 wt% or less, B: 0.0020 wt% or less,
O: 0.0020 wt% or less, N: 0.0020 wt%
Less than, Cr: 0.001 to 0.05 wt%, Co: 1w
more than t% to 7 wt%, the balance Fe and unavoidable impurities, and is 0.
Fe-for a shadow mask excellent in press formability, characterized by having a 2% proof stress of 28.0 kgf / mm ² or less and a degree of integration of {211} crystal faces on the plate surface of 16% or less.
Ni-Co alloy thin plate.

(3) After hot-rolling the hot-rolled sheet having the component composition described in (1 ) above at 910 to 990 ° C.,
The final recrystallization annealing is performed through the steps of cold rolling-recrystallization annealing-cold rolling, and then the following expression is satisfied according to the average austenite crystal grain size D (μm) after the final recrystallization annealing. Finish cold rolling is performed at a rolling ratio R (%) of 16 ≦ R ≦ 75 6.38D-133.9 ≦ R ≦ 6.38D-51.0, and then the softening annealing before press forming is performed at an annealing temperature: 790 ° C
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni of 28.0 kgf / mm ² or less and the degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing a Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a thin alloy plate.

(4) After hot-rolling the hot-rolled sheet having the component composition described in (1 ) above at 910 to 990 ° C.,
The final recrystallization annealing is performed through the steps of cold rolling-recrystallization annealing-cold rolling, and then the following expression is satisfied according to the average austenite crystal grain size D (μm) after the final recrystallization annealing. Finish cold rolling is performed at a rolling ratio R (%) of 21 ≦ R ≦ 70 6.38D-122.6 ≦ R ≦ 6.38D-65.2 Then, the softening annealing before press forming is performed at an annealing temperature: 790 ° C
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni with 27.5 kgf / mm ² or less and a degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing a Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a thin alloy plate.

(5) After hot-rolling the hot-rolled sheet having the component composition described in (1 ) above at 910 to 990 ° C.,
The final recrystallization annealing is performed through the steps of cold rolling-recrystallization annealing-cold rolling, and then the following expression is satisfied according to the average austenite crystal grain size D (μm) after the final recrystallization annealing. Finishing cold rolling is performed at a rolling ratio R (%) of 26 ≦ R ≦ 63 6.38D−108.0 ≦ R ≦ 6.38D−79.3, and then softening annealing before press forming is performed at an annealing temperature: 790 ° C
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni of 27.0 kgf / mm ² or less, and the degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing a Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a thin alloy plate.

(6) After hot-rolling the hot-rolled sheet having the composition as described in (2 ) above at 910 to 990 ° C.,
The final recrystallization annealing is performed through the steps of cold rolling-recrystallization annealing-cold rolling, and then the following expression is satisfied according to the average austenite crystal grain size D (μm) after the final recrystallization annealing. Finish cold rolling is performed at a rolling ratio R (%) of 16 ≦ R ≦ 75 6.38D-133.9 ≦ R ≦ 6.38D-51.0, and then the softening annealing before press forming is performed at an annealing temperature: 790 ° C
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni of 28.0 kgf / mm ² or less and the degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing an Fe-Ni-Co alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a -Co alloy thin plate.

(7) After annealing the hot-rolled sheet having the component composition described in (2 ) above at 910 to 990 ° C.,
The final recrystallization annealing is performed through the steps of cold rolling-recrystallization annealing-cold rolling, and then the following expression is satisfied according to the average austenite crystal grain size D (μm) after the final recrystallization annealing. Finish cold rolling is performed at a rolling ratio R (%) of 21 ≦ R ≦ 70 6.38D-122.6 ≦ R ≦ 6.38D-65.2 Then, the softening annealing before press forming is performed at an annealing temperature: 790 ° C
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni with 27.5 kgf / mm ² or less and a degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing an Fe-Ni-Co alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a -Co alloy thin plate.

(8) After hot-rolling the hot-rolled sheet having the composition described in (2 ) above at 910 to 990 ° C.,
The final recrystallization annealing is performed through the steps of cold rolling-recrystallization annealing-cold rolling, and then the following expression is satisfied according to the average austenite crystal grain size D (μm) after the final recrystallization annealing. Finishing cold rolling is performed at a rolling ratio R (%) of 26 ≦ R ≦ 63 6.38D−108.0 ≦ R ≦ 6.38D−79.3, and then softening annealing before press forming is performed at an annealing temperature: 790 ° C
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni of 27.0 kgf / mm ² or less, and the degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing an Fe-Ni-Co alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a -Co alloy thin plate.

[0016]

The details of the present invention and the reasons for limitation thereof will be described below. In the present invention, the softening annealing before press forming (hereinafter, referred to as before pressing) The 0.2% proof stress at room temperature after carrying out the (annealing) is determined to be 28.0 kgf / mm ² or less. Note that 0.2% proof stress is 28.0 kgf / m
By further reducing it in the range of m ² or less, the shape fixability at the time of press molding can be made more excellent.
In the essence of the present invention, by limiting the content of B and O mainly to a specific range, the crystal grain growth property under the specific pre-annealing conditions premised by the present invention is increased, and the graininess is increased. Secures a lower yield strength and mainly limits the contents of Si and N within a specific range, thereby making the mold fit well during press molding and suppressing the occurrence of galling on the mold. By controlling the degree of integration of {211} crystal planes on the surface of the plate after the reduction of strength and the annealing before pressing to a predetermined range, it is possible to suppress cracking of the material during press forming.

First, the reasons for limiting the component composition of the alloy will be described. 30-100 ° C required for Fe-Ni alloy thin plate for shadow mask to prevent color shift
The upper limit of the average coefficient of thermal expansion in the temperature range of
(1/10 ⁶ ) / ° C. The thermal expansion coefficient depends on the Ni content of the alloy, and the Ni content for satisfying the above condition of the average thermal expansion coefficient is 34 to 38 wt%. Therefore, Ni is 3
The range is 4 to 38 wt%. Further, in order to obtain a lower average thermal expansion coefficient, it is desirable that the Ni content is 35 to 37 wt%, and more preferably 35.5 to 36.5 wt%. Co is usually contained in the Fe—Ni-based alloy to some extent as an unavoidable impurity, and when Co is 1 wt% or less, it hardly affects the characteristics, and the amount of Ni may be in the above range. On the other hand, when Co is contained in an amount of more than 1 wt% to 7 wt%, Ni for satisfying the above condition of the average thermal expansion coefficient.
Is in the range of 28 to 38 wt%. Therefore, Co is 1w
In the case of containing more than t% to 7 wt%, Ni is 28 to 38
The range is wt%. In addition, Co is 3 to 6 wt%, Ni
When the content is 30 to 33 wt%, more excellent characteristics can be obtained. On the other hand, if Co exceeds 7 wt%, the thermal expansion coefficient deteriorates, so the upper limit of Co is 7 wt%.

O is one of the unavoidable impurity elements, and when the amount of O is large, the amount of oxide-based nonmetallic inclusions in the alloy is large, and this inclusion grows in crystal grains during pre-press annealing, especially 79
This impedes the crystal grain growth under the pre-press annealing conditions of 0 ° C. or less and 40 minutes or less, which is the premise of the present invention. If O exceeds 0.0020 wt%, the inhibitory effect on the grain growth becomes remarkable, and 28.0 kgf / mm after pre-press annealing.
0.2% yield strength of ² or less cannot be obtained. Therefore, O is 0.
The upper limit is 0020 wt%. The lower limit is not particularly limited, but from the viewpoint of economical efficiency in melting, about 0.001 wt% is a practical lower limit.

B has the effect of improving hot workability, but if its content increases, it segregates at the grain boundaries of the recrystallized grains formed during pre-press annealing and inhibits grain boundary migration. As a result, the crystal grain growth is hindered, and the desired 0.2% proof stress after the pre-press annealing cannot be obtained. In particular, under the pre-press annealing condition which is the premise of the present invention, the grain growth inhibitory action is strong, and this action does not work uniformly for all the crystal grains, resulting in significant mixed grain A structure is generated, and unevenness in the elongation of the material during press molding also occurs. In addition, B has the effect of increasing the degree of integration of the {211} crystal faces after pre-press annealing that causes cracking of the material skirt portion. When the amount of B exceeds 0.0020 wt%, the above grain growth inhibitory effect becomes remarkable, so 28.0 kgf / mm
A 0.2% proof stress of ² or less cannot be obtained, and problems such as unevenness in elongation at the time of press molding occur, and in addition, the degree of integration of {211} crystal faces exceeds the upper limit defined by the present invention. Therefore, B is 0.0020 wt% or less.

Si is added as a deoxidizing element at the time of melting. If the added amount exceeds 0.05 wt%, an oxide film of Si is formed on the surface of the alloy plate during annealing before pressing, and this oxide film causes Familiarity with the mold during press molding deteriorates,
The galling of the alloy plate to the mold will occur. Therefore, the upper limit of Si is 0.07 wt%. Further, by further reducing the amount of Si, the alloy plate and the mold can be made more compatible with each other. Although the lower limit of Si is not particularly limited, it is 0.
The practical lower limit is about 001 wt%.

N is an element that is inevitably mixed in during melting. If N is contained in an amount of 0.0020 wt% or more, N is concentrated on the surface of the alloy plate during pre-press annealing to form a nitride, which is pressed by the nitride. Familiarity with the mold at the time of molding becomes poor, and galling of the alloy plate to the mold occurs.
Therefore, N is set to less than 0.0020 wt%. Note that N
The lower limit is not particularly limited, but from the viewpoint of economical efficiency in melting, about 0.0001 wt% is a practical lower limit. In addition,
For elements other than the above component elements, C: 0.000
1 to 0.0050 wt%, Mn: 0.001 to 0.35
It is preferable to set it in the range of wt% and Cr: 0.001 to 0.05 wt%.

By satisfying the above component conditions and 0.2% proof stress after press pre-annealing, it is possible to suppress the galling of the mold during press molding and to make the shape fixability excellent. However, this alone does not improve the problem of material cracking, another aspect of press formability. In order to solve such a problem, the present inventors have
Alloy plates having a component composition within the range of the present invention and a 0.2% proof stress and different crystal orientations on the plate surface were prepared, and the relationship between the crystal orientation on the plate surface and the occurrence of cracks during press forming was investigated.
As a result, in order to suppress cracking of the alloy sheet, not only the 0.2% proof stress of the alloy sheet after annealing before pressing is specified, but also the degree of integration of {211} crystal planes on the sheet surface is controlled to be below a specific value. Found that it is necessary to do.

FIG. 1 shows the occurrence of cracks in the alloy plate during press forming and {2
11} shows the relationship between the degree of integration of crystal planes and 0.2% proof stress. The degree of integration of {211} crystal planes is (111), (200), (220), (31) as the relative X-ray diffraction intensity ratio of the (422) diffraction plane of the alloy plate after annealing before pressing.
Relative X of each diffraction surface of 1), (331) and (420)
It was calculated by dividing by the sum of the line intensity ratios. Where relative X
The line diffraction intensity ratio is the X-ray diffraction intensity measured on each diffraction surface divided by the theoretical X-ray diffraction intensity of that diffraction surface. For example, the relative X-ray diffraction intensity ratio of the (111) diffraction plane is (11
1) X-ray diffraction intensity of the diffractive surface divided by theoretical X-ray diffraction intensity of the (111) diffractive surface. The degree of integration of the {211} crystal plane was measured by measuring the X-ray diffraction intensity of a (422) diffraction plane which is equivalent to the {211} plane in terms of orientation.

According to FIG. 1, the 0.2% proof stress is 28.0 k.
gf / mm ² or less and the degree of integration of {211} crystal faces is 1
If it is 6% or less, cracking of the alloy plate does not occur during press forming, and the excellent effect intended by the present invention is obtained. For the above reasons, in the present invention, as a condition for suppressing cracking of the alloy plate, {211} on the plate surface after annealing before pressing is used.
The degree of crystal plane integration is defined as 16% or less.

The alloy thin sheet of the present invention is obtained by subjecting a hot rolled sheet having the above-described composition to the hot rolled sheet annealing, and then the final recrystallization annealing through the steps of cold rolling-recrystallization annealing-cold rolling. ,
Then, finish cold rolling is carried out, and thereafter, pre-press annealing is carried out to manufacture the steel sheet. First, the hot-rolled sheet annealing needs to be performed within a specific temperature range so that the degree of integration of {211} crystal faces is 16% or less. Hot-rolled sheets satisfying the component conditions of the present invention are annealed at various temperatures, and cold rolling-recrystallization annealing-cold rolling-recrystallization annealing (890 ° C x
An alloy plate was manufactured in the manufacturing process of 1 minute) -finish cold rolling (rolling rate 21%)-annealing before press (750 ° C x 20 minutes).
For comparison, an alloy sheet was produced from a hot-rolled sheet that was not subjected to hot-rolled sheet annealing by the same production process. FIG. 2 shows the relationship between the degree of integration of {211} crystal planes on the plate surface of the obtained alloy plate and the elongation by the tensile test, and the annealing temperature of the hot rolled plate. According to this, when the hot-rolled sheet annealing temperature is 910 to 990 ° C, {2
11} The degree of integration of crystal faces is 16% or less. Therefore, in the present invention, the hot rolled sheet annealing temperature is 910 to 910 as a condition for making the degree of integration of {211} crystal planes 16% or less.
It is specified as 990 ° C.

In order to obtain the degree of integration of the {211} crystal planes defined by the present invention, it is not preferable to perform the slab homogenization heat treatment after the slabbing in the manufacturing process. For example,
When the slab homogenization heat treatment is performed at 1200 ° C. or higher for 10 hours or longer, the degree of integration of {211} crystal planes exceeds the specified value of the present invention, so such treatment must be avoided. . The degree of integration of the {211} crystal plane is 16
%, The mechanism of material cracking during press forming is not necessarily clear. However, looking at the elongation in the direction perpendicular to the rolling shown in FIG. Since the elongation shows a low value, it is considered that if the degree of integration of the {211} crystal plane becomes higher, the elongation in the direction perpendicular to the rolling decreases and the fracture limit becomes lower, so that cracking may occur.

The degree of integration of {211} crystal faces after annealing before pressing is set to 16% or less and the 0.2% proof stress is 28.0 Kgf.
In order to achieve a value of / mm ² or less, it is important to control finish cold rolling conditions (finish cold rolling ratio) and pre-press annealing conditions in addition to the above-mentioned regulations. FIG. 3 shows a hot-rolled sheet that satisfies the component conditions of the present invention and is annealed from a hot-rolled sheet (910 to 990 ° C.)-Cold rolling-recrystallization annealing-cold rolling-recrystallization annealing-finish cold rolling-before pressing. 0.2% by a tensile test on the alloy plate manufactured through the manufacturing process of annealing (750 ° C. × 15 minutes)
The yield strength (numerical value in parentheses in the figure) was measured, and this is shown by the relationship between the finish cold rolling ratio and the average austenite grain size before finish cold rolling. In this test, a predetermined average austenite grain size was obtained by changing the recrystallization annealing temperature before finish cold rolling.

According to FIG. 3, the finish cold rolling rate R (%) is 1
In the range of 6 to 75% and according to the average austenite crystal grain size D (μm) before finish cold rolling, 6.38D-133.9 ≦ R ≦ 6.38D-51.0 (that is, It is understood that the 0.2% proof stress can be set to 28.0 Kgf / mm ² or less by setting the area I in the figure). When the finish cold rolling rate R is less than 16% or 6.38D-133.9> R, recrystallization is insufficient under the pre-press annealing conditions specified in the present invention,
Moreover, the grain growth of the recrystallized grains is also insufficient, so the 0.2% proof stress exceeds 28.0 Kgf / mm ² . On the other hand, the finish cold rolling rate R exceeds 75% or R> 6.38D-5
In the case of 1.0, 100% recrystallization is carried out under the pre-press annealing condition specified in the present invention, but the frequency of nucleation during recrystallization becomes too high, and the recrystallized grains become fine. The 2% proof stress exceeds 28.0 Kgf / mm ² .

For the above reasons, in the present invention, 28.0 Kgf / m under the pre-press annealing conditions specified by the present invention.
As the finish cold rolling condition for obtaining 0.2% yield strength of m ² or less, the following formulas (1a) and (1b) are satisfied according to the average austenite crystal grain size D (μm) before finish cold rolling. The finish cold rolling rate R (%) is specified. 16 ≦ R ≦ 75 (1a) 6.38D-133.9 ≦ R ≦ 6.38D-51.0 (1b) Further, the appropriateness according to the average austenite crystal grain size before such finish cold rolling. If the finish cold rolling rate R (%) is within the range, {211} of the surface of the alloy plate after annealing before pressing
The degree of integration of crystal planes can be 16% or less.

In order to control the texture of the alloy sheet of the present invention as described above, in addition to the texture control in hot-rolled sheet annealing, an appropriate finish cold rolling rate according to the crystal grain size before finish cold rolling is used. The reason is that the frequency of nucleation during recrystallization is properly controlled. According to FIG. 3, by optimizing the finish cold rolling rate R (%) according to the average austenite crystal grain size D before finish cold rolling, the 0.2% yield strength after pre-press annealing was lowered. It turns out that it is possible to do. That is, 21 ≦ R ≦ 70 (2a) 6.38D-122.6 ≦ R ≦ 6.38D-65.2 (2b) (that is, within region II in the figure) The 2% proof stress can be 27.5 Kgf / mm ² or less, and further 26 ≦ R ≦ 63 (3a) 6.38D-108.0 ≦ R ≦ 6.38D-79.3 (3b). (That is, within the region III in the figure), the 0.2% proof stress can be reduced to 27.0 Kgf / mm ² or less.

Therefore, in the present invention, 0.2% proof stress: 2
A finish cold rolling condition that achieves 7.5 Kgf / mm ² or less is as follows: the finish cold rolling satisfying the above formulas (2a) and (2b) according to the average austenite crystal grain size D (μm) before finish cold rolling. Rolling rate R (%), 0.2% yield strength: 2
As finishing cold rolling conditions that can obtain 7.0 Kgf / mm ² or less, finish cold rolling satisfying the above formulas (3a) and (3b) according to the average austenite crystal grain size D (μm) before finish cold rolling is performed. The rolling ratio R (%) is specified. In addition,
The average austenite grain size D before finish cold rolling, which is defined by the relationship with the finish cold rolling rate R, is obtained by annealing the hot rolled sheet by hot rolling and annealing after the subsequent cold rolling. 860
˜950 ° C., annealing time: It can be obtained by appropriately selecting in the range of 0.5 to 2 minutes.

FIG. 4 shows the finish cold rolling ratio according to the composition of components, the hot rolled sheet annealing conditions, and the average austenite grain size before finish cold rolling within the scope of the present invention. 910-990 ° C.)-Cold rolling-recrystallization annealing-cold rolling-recrystallization annealing-finishing cold rolling-annealing temperature T of pre-press annealing for an alloy sheet manufactured through the manufacturing steps of pre-press annealing. 3 shows the relationship between the annealing time t, the 0.2% proof stress after annealing before pressing and the degree of integration of {211} crystal faces. According to FIG. 4, even if the finish cold rolling rate according to the hot rolled sheet annealing conditions and the average austenite grain size before finish cold rolling is within the range of the present invention, T <−53.8 log t +.
In 806, recrystallization was not sufficient, so the 0.2% proof stress exceeded 28.0 Kgf / mm ² , and {211}.
The degree of integration of crystal planes exceeds 16%. Further, when the annealing temperature T exceeds 790 ° C. or the annealing time t exceeds 40 minutes, the {211} crystal plane develops, so that the integration degree of this crystal plane exceeds 16%. For the above reason, in the present invention, the annealing temperature T: 7 is used as the pre-press annealing condition for obtaining the desired 0.2% proof stress and the degree of integration of {211} crystal faces.
90 ° C. or less, annealing time t: 40 minutes or less, T ≧ −53.8
log t + 806.

FIG. 5 shows the alloy of the present invention (alloy No. of the example).
1) and comparative alloys (alloy Nos. 21 and N of the examples)
o. 22), using these hot rolled sheets, hot rolled sheet annealing (910 to 990 ° C.)-Cold rolling-recrystallization annealing-cold rolling-recrystallization annealing-finishing cold rolling-pre-press annealing. Of the alloy sheet manufactured through the manufacturing process of No. 2 above, the change in 0.2% proof stress and the degree of integration of {211} crystal faces depending on the annealing time of pre-press annealing is shown for each annealing temperature. It should be noted that all alloys have a finish cold rolling ratio according to the hot-rolled sheet annealing conditions and the average austenite crystal grain size before finish cold rolling within the scope of the present invention. According to FIG. 5, in the alloy of the present invention, the 0.2% proof stress and the degree of integration of the {211} crystal planes defined by the present invention are obtained under the pre-press annealing conditions within the scope of the present invention described above. On the other hand, in the comparative alloy, the 0.2% proof stress exceeds 28.0 Kgf / mm ² even when annealed at 750 ° C., and the degree of accumulation of {211} crystal faces also exceeds 16%. Has been shown to have problems.
As described above, in the present invention, it is found that it is extremely important to set the component composition of the alloy to the predetermined condition in addition to the regulation of the manufacturing conditions.

The pre-press annealing defined by the present invention may be carried out before the photo-etching, and if the pre-press annealing condition is within the scope of the present invention, the quality of the photo-etching is not deteriorated. In conventional materials, pre-press annealing cannot be performed before photo-etching because photo-etching quality is impaired when photo-etching is performed after performing pre-press annealing under the conditions specified by the present invention. . On the other hand, in the material of the present invention having a specific component composition and a degree of integration of {211} crystal faces, the etching property is not impaired even if photoetching is performed after pre-press annealing. In addition to the methods described above, methods of obtaining the degree of integration of {211} crystal planes defined by the present invention include the adoption of rapid solidification, texture control by controlling recrystallization in hot working, and the like.

[0035]

【Example】

[Example 1] Alloy No. having the chemical composition shown in Tables 1 and 2 was obtained by ladle refining. 1-No. Adjust 23, alloy N
o. 1-No. 13, No. 18-No. For No. 23, cast it into an ingot, and after caring for these ingots,
Slump rolling, surface flaw removal, hot rolling (heating conditions: 1100
(° C x 3 hr) to obtain a hot rolled sheet. In addition, alloy No. 14
~ No. Regarding No. 17, the thin cast plate was directly cast, and the thin cast plate was hot-rolled at a temperature of 1300 to 1000 ° C. at a reduction rate of 40% and then wound at 700 ° C. to obtain a hot-rolled plate. For these hot-rolled sheets, hot-rolled sheet annealing (930 ° C.)-Cold rolling-recrystallization annealing-cold rolling-recrystallization annealing (annealing under the conditions shown in Table 5) -finishing cold rolling (rolling rate 21 %) In order to obtain an alloy plate having a plate thickness of 0.25 mm. The hot rolled sheet was sufficiently recrystallized at the stage after hot rolling. After processing these alloy plates into a flat mask by etching,
Pre-press annealing was performed under the condition of 750 ° C. × 20 minutes, and the material No.
1-No. I got 23. Press molding was performed on these materials to examine press moldability. Tables 1 and 2 show the average austenite crystal grain size of each material before finish cold rolling, and Tables 3 and 4 show the degree of integration of {211} crystal faces, tensile properties and press formability. The tensile properties (0.
The 2% proof stress and the elongation in the direction perpendicular to the rolling direction) and the degree of integration of {211} crystal planes were examined for the alloy sheet after annealing before pressing.
Tensile properties were measured at room temperature, and
1} The measurement of the integration degree of the crystal plane is based on the X-ray diffraction described above.

According to Tables 3 and 4, the composition of components satisfying the conditions of the present invention, the degree of accumulation of {211} crystal faces, and 0.
Material No. with 2% proof stress 1-No. All of them show excellent press formability, and the material No. 13 which is an example of the present invention and contains Co. 14-No. Similarly, 17 also shows excellent characteristics. On the other hand, the material No. 1
8 and No. No. 20 is a comparative example in which the amount of Si and the amount of N exceeded the range of the present invention, respectively, and both have problems in compatibility with the mold. Material No. No. 19 is a comparative example in which the O content exceeds the range of the present invention, and the 0.2% proof stress is 28.9 Kgf /
Since it exceeds mm ² , the shape fixability is inferior, and the alloy plate also cracks. In addition, the material No. 21 and No. No. 22 is a comparative example in which only the B content and the B content and the O content exceeded the range of the present invention, respectively, and each had a 0.2% proof stress of 2
Since it exceeds 8.0 kgf / mm ² , the shape fixability is poor. Further, in these comparative examples, the degree of integration of the {211} crystal planes exceeds the range of the present invention, so that the alloy plate also cracks. Material No. In No. 23, the average austenite grain size before finish cold rolling did not reach the level satisfying the condition of the finish cold rolling rate R defined by the present invention, and therefore the 0.2% proof stress was 28.0 kgf / mm ² Shape inferiority is inferior and the alloy plate is cracked. As described above, the component composition satisfying the conditions of the present invention, {211}
By setting the degree of crystal plane integration and the 0.2% proof stress,
Fe- having excellent press formability which is the object of the present invention
It can be seen that the Ni-based alloy thin plate and the Fe-Ni-Co-based alloy thin plate can be obtained.

Example 2 Alloy No. used in Example 1
1, No. 9, No. 14 hot-rolled sheets were used, and those hot-rolled sheets were annealed at the temperatures shown in Table 6 and those that were not hot-rolled were cold-rolled-
Recrystallization annealing-Cold rolling-Recrystallization annealing (890 ° C x 1 minute)
-Finishing cold rolling (rolling rate 21%) was sequentially performed to obtain an alloy plate having a plate thickness of 0.25 mm. After each alloy plate was processed into a flat mask by etching, it was annealed before press under the condition of 750 ° C. × 20 minutes, and the material No. 24 to 28 were obtained.
Press molding was performed on these materials to examine press moldability. Table 6 shows the hot-rolled sheet annealing temperature of each material, the average austenite crystal grain size before finish cold rolling and the degree of integration of {211} crystal faces, and Table 7 shows the tensile properties and press formability. The method of measuring each characteristic value is the same as in Example 1.

According to Tables 6 and 7, the material Nos. Satisfying the component conditions and manufacturing conditions of the present invention are shown. 24, No. 25
Shows excellent press formability. On the other hand, the material No. 26-No. 28 is a comparative example in which the hot-rolled sheet annealing temperature is less than the lower limit of the present invention, a comparative example in which the hot-rolled sheet annealing temperature exceeds the upper limit of the present invention, and a comparative example in which the hot-rolled sheet annealing is not performed, and both are {211. } The degree of integration of crystal planes exceeds the upper limit defined by the present invention, and the alloy plate is cracked during press forming. In addition, the material No. 28 is 0.2%
The yield strength exceeds 28.0 Kgf / mm ^2, and the shape fixability during press molding is also poor. As described above, in order to bring the degree of integration of {211} crystal faces into the range of the present invention, it is important to carry out hot-rolled sheet annealing according to the conditions of the present invention.

Example 3 Alloy No. used in Example 1
1, No. 2, No. 4, No. 6, No. 7, No.
8, No. 9, No. 11, No. 12, No. 13 and No. 14 hot rolled sheets were used, and hot rolled sheet annealing (930 ° C.)-Cold rolling-recrystallization annealing-for these hot rolled sheets
Cold rolling-recrystallization annealing (at the temperatures shown in Table 8 and Table 1
Minute hold) -finish cold rolling is sequentially performed, and the plate thickness is 0.25 m.
An alloy plate of m was obtained. After these alloy plates were processed into flat masks by etching, they were annealed before pressing under the conditions of 750 ° C. × 20 minutes, and the material No. 29-No. I got 66. These materials were press-molded and the press-moldability was examined. Tables 8 and 9 show the annealing temperature of each material before finish cold rolling, the average austenite grain size before finish cold rolling, the finish cold rolling rate and the tensile properties, and Tables 10 and 11 show {211 } Shows the degree of integration of crystal faces and press formability. The method of measuring each characteristic value is the same as in Example 1.

According to Tables 8 to 11, the composition conditions, hot-rolled sheet annealing conditions and pre-press annealing conditions of the present invention are satisfied,
A material No. having a relationship between the average austenite grain size before finish cold rolling and the finish cold rolling rate is within the range defined by the present invention. 30-No. 35, No. 38, No. 41-N
o. 43, No. 47-No. 66 are both {21
1} The degree of integration of crystal faces is 16% or less. Of these, the material No. 30, No. 35, No. 38, No. Four
1, No. 47, No. 49, No. 50, No. 5
4, No. 60, No. 63 and No. Reference numeral 66 is an example of the present invention manufactured at a finish cold rolling rate R (range of region I in FIG. 3) satisfying the above-described formulas (1-a) and (1-b), and 0.2%. The yield strength is 28.0 Kgf / mm ² or less. In addition, the material No. 31, No. 33, No. Three
4, No. 43, No. 48, No. 52, No. 5
5, No. 59 and No. 59. 65 is the above-mentioned (2-
Finishing cold rolling rate R satisfying equations a) and (2-b)
It is an example of the present invention manufactured in (range of region II in FIG. 3), and has a 0.2% proof stress of 27.5 kgf / mm ² or less. Further, the material No. 32, No. 42, No. 5
1, No. 53, No. 56, No. 57, No. 5
8, No. 61, No. 62 and No. 62. 64 is an example of the present invention manufactured at a finish cold rolling rate R (range of region III in FIG. 3) satisfying the above-mentioned formulas (3-a) and (3-b), and 0.2%. Proof strength is 27.0 kgf / mm ²
It is the following. As described above, the 0.2% proof stress defined by the present invention is obtained for all the materials, and excellent press formability is exhibited. It is also found that the lowering of the 0.2% proof stress provides more excellent shape fixability.

On the other hand, the material No. 29, No. Three
6, No. 37, No. 39, No. 40, No. 44
And No. No. 45 is a compositional condition within the scope of the present invention, a hot rolled sheet annealing condition and a pre-press annealing condition, but the relationship between the average austenite grain size before finish cold rolling and the finish cold rolling rate is defined by the present invention. These are comparative examples deviating from the region where either one or both of 0.2% proof stress and the degree of integration of {211} crystal planes exceed the stipulated conditions of the present invention, and the shape fixability at the time of press molding. One or both of the cracking of the alloy sheet and the alloy sheet has a problem. Material No. No. 46 has an average austenite grain size of 10.0 μm because the annealing condition before finish cold rolling is 850 ° C. × 1 minute, and the 0.2% proof stress is 28.0 kgf / mm at a finish cold rolling rate of 15%. ^It exceeds ^2, and the shape fixability during press molding is poor. As mentioned above,
Even if the component conditions of the present invention, the hot rolled sheet annealing conditions and the pre-press annealing conditions are satisfied, the relationship between the average austenite grain size and the finish cold rolling rate before finish cold rolling is from the region defined by the present invention. It can be seen that if it comes off, excellent press formability cannot be obtained.

Example 4 Alloy No. used in Example 1
1, No. 4, No. 9, No. 10, No. 12, N
o. 14, No. 21 and No. No. 22, hot-rolled sheet was used, and the hot-rolled sheet was annealed (930 ° C.)-
Cold Rolling-Recrystallization Annealing-Cold Rolling-Recrystallization Annealing (890
(° C x 1 min) -finish cold rolling (rolling rate 21%) were sequentially carried out to obtain an alloy plate having a plate thickness of 0.25 mm. After processing these alloy plates into a flat mask by etching,
Pre-press annealing was performed under the conditions shown in Table 12, and the material No. 67-
84 was obtained. These materials were press-molded and the press-moldability was examined. Table 12 shows the average austenite crystal grain size before finish cold rolling, annealing conditions before press, degree of accumulation of {211} crystal faces, tensile properties and press formability. In addition,
The method of measuring each characteristic value is the same as that in the first embodiment.

According to Table 12, the component conditions of the present invention, hot-rolled sheet annealing conditions and finish cold rolling conditions (finish cold rolling ratio).
And the annealing conditions (temperature, time) before pressing within the specified range of the present invention are satisfied. 67, No. 69, No.
70 and No. 70. 76-No. 84 are both {21
1} The degree of integration of crystal planes is 16% or less, and the 0.2% proof stress is also within the specified range of the present invention, showing excellent press molding quality. On the other hand, the material No. 72 and N
o. No. 73 is a component example of the present invention, a hot rolled sheet annealing condition and a finish cold rolling condition (finish cold rolling ratio), but with respect to pre-press annealing, a comparative example in which the annealing temperature exceeded the upper limit of the present invention, This is a comparative example in which the annealing time exceeds the upper limit of the present invention, and the degree of integration of {211} crystal faces is 16% in all cases.
And the alloy plate is cracked. Also, the material N
o. No. 68 is a comparative example in which the annealing temperature T of the pre-press annealing and the annealing time t do not satisfy the conditional expression (T ≧ −53.8log t + 806) of the present invention, No. 68. Reference numeral 71 is a comparative example in which the annealing time of pre-press annealing exceeds the upper limit of the present invention, and the annealing temperature T and the annealing time t do not satisfy the above conditional expressions, and all the comparative examples have a 0.2% proof stress of 28.0 kgf. / Mm ² is exceeded, the shape fixability during press forming is poor, and the degree of accumulation of {211} crystal faces exceeds 16%, and cracking of the alloy plate occurs during press forming.

Material No. 74 and No. 74. No. 75 is a comparative example using a comparative alloy, and these are 6 at 750 ° C.
0.2% even when pre-press annealing of 0 min is performed
The yield strength is more than 28.0 kgf / mm ² , and the shape fixability during press molding is poor. In addition, {2 of these materials
11} The degree of integration of crystal planes exceeds 16%, and the alloy plate also cracks during press forming. As described above, even if the component conditions of the present invention, hot-rolled sheet annealing conditions and finish cold rolling conditions are satisfied, if the pre-press annealing conditions deviate from the scope of the present invention, excellent press formability is obtained. I know I can't.

Example 5 Alloy No. used in Example 1
1, No. 4 using the hot-rolled sheet of No. 4, hot-rolled sheet annealing (930 ℃) -cold rolling-recrystallization annealing-
Cold rolling-recrystallization annealing (890 ° C x 1 min) -finishing cold rolling (rolling rate 21%) were sequentially carried out to obtain a plate thickness of 0.25 m.
An alloy plate of m was obtained. These alloy plates were annealed before press under the conditions shown in Table 13, and the material No. 85-No. I got 87. After processing these materials into flat masks by etching, press molding was performed to examine press moldability. Table 13 shows the average austenite crystal grain size before finish cold rolling of each material, the pre-press annealing conditions and the degree of integration of {211} crystal faces, and Table 14 shows the tensile properties, press formability and etching properties. The etching property was examined by visually observing the occurrence of unevenness of the flat mask after etching. Moreover, the measuring method of other characteristic values is the same as that of the first embodiment.

According to Tables 13 and 14, the material Nos. Satisfying the component conditions and manufacturing conditions of the present invention are shown. 85-N
o. No. 87 has a good etching property, and the degree of integration of {211} crystal planes is 16% or less and 0.
The 2% proof stress is also within the specified range of the present invention, and shows excellent press formability. As described above, excellent press formability is obtained by satisfying the component conditions and the production conditions of the present invention, and there is no unevenness in the obtained flat mask even when etching is performed after pre-press annealing, It can be seen that good etching properties can be obtained. In addition, as shown in the first to fifth embodiments described above, {211}
In the comparative example in which the degree of integration of crystal planes exceeds 16%, the elongation in the direction perpendicular to the rolling after annealing before pressing is lower than that of the example of the present invention. It is presumed that the elongation in the direction perpendicular to the rolling after annealing decreases and cracking occurs during press forming.

[0047]

[Table 1]

[0048]

[Table 2]

[0049]

[Table 3]

[0050]

[Table 4]

[0051]

[Table 5]

[0052]

[Table 6]

[0053]

[Table 7]

[0054]

[Table 8]

[0055]

[Table 9]

[0056]

[Table 10]

[0057]

[Table 11]

[0058]

[Table 12]

[0059]

[Table 13]

[0060]

[Table 14]

[0061]

As described above, the Fe-Ni-based alloy thin plate and the Fe-Ni-Co-based alloy thin plate for a shadow mask according to the present invention are subjected to annealing before press at a low temperature of 720 ° C to 790 ° C for 40 minutes or less. Even if it is performed with a short annealing time of
It exhibits excellent press formability, that is, excellent shape fixability at the time of forming, good compatibility with a mold, and excellent press formability without material cracking. Further, in the alloy thin plate of the present invention, the required etching property and press formability can be obtained even when pre-press annealing is performed before etching. Therefore, if pre-press annealing is performed in advance, the press on the side of the cathode ray tube maker Since pre-annealing can be omitted, this is also an invention with great economic merit for users of alloy sheets. Further, according to the manufacturing method of the present invention, such an alloy thin plate can be easily manufactured.

[Brief description of drawings]

FIG. 1 0.2% proof stress after annealing before press and {21
1} Graph showing the relationship between the degree of integration of crystal faces and the occurrence of cracks during press molding

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

FIG. 3 is a graph showing the relationship between the average austenite grain size before finish cold rolling and the finish cold rolling ratio, and the 0.2% proof stress after annealing before pressing.

[Fig. 4] Pre-press annealing condition and 0.2% after pre-press annealing
Graph showing the relationship between proof stress and degree of integration of {211} crystal planes

[Fig. 5] Pre-press annealing conditions and 0.2% after pre-press annealing
Graph showing the relationship between proof stress and degree of integration of {211} crystal planes

─────────────────────────────────────────────────── ─── Continuation of the front page (56) Reference JP-A-5-209254 (JP, A) JP-A-6-158229 (JP, A) JP-A-6-57384 (JP, A) JP-A-5- 65598 (JP, A) JP 62-185860 (JP, A) JP 4-354853 (JP, A) JP 64-25944 (JP, A) JP 4-341543 (JP, A) JP-A-3-202446 (JP, A) JP-A-4-358042 (JP, A) JP-A 64-52022 (JP, A) JP-A 62-149819 (JP, A) (58) Fields investigated (Int.Cl. ⁷ , DB name) C22C 38/00-38/60 H01J 29/07

Claims (8)

(57) [Claims] 1. Ni: 34 to 38 wt%, Si: 0.0
7 wt% or less, B: 0.0020 wt% or less, O: 0.
0020 wt% or less, N: less than 0.0020 wt%, C
r: 0.001 to 0.05 wt % , Co: 1 wt% or less, balance Fe and unavoidable impurities, and 0.2% proof stress after performing softening annealing before press molding is 28.
An Fe-Ni alloy thin plate for a shadow mask excellent in press formability, which has an accumulation degree of {211} crystal planes of 16% or less on the plate surface of 0 kgf / mm ² or less. 2. Ni: 28 to 38 wt%, Si: 0.0
7 wt% or less, B: 0.0020 wt% or less, O: 0.
0020 wt% or less, N: less than 0.0020 wt%, C
r: 0.001 to 0.05 wt % , Co: more than 1 wt%
7 wt%, balance Fe and unavoidable impurities, 0.2% proof stress after softening annealing before press forming is 28.0 kgf / mm ² or less, and the degree of accumulation of {211} crystal faces on the plate surface is 16 % Or less, a Fe-Ni-Co alloy thin plate for a shadow mask excellent in press formability. 3. A hot-rolled sheet having the component composition according to claim 1 is annealed at 910 to 990 ° C., and then subjected to the steps of cold rolling-recrystallization annealing-cold rolling for final re-rolling. Crystal annealing is carried out, and then finish cold rolling is carried out at a rolling ratio R (%) satisfying the following formula in accordance with the average austenite crystal grain size D (μm) after the final recrystallization annealing, and 16 ≦ R ≦ 75 6.38D-133.9 ≦ R ≦ 6.38D-51.0 Then, the softening annealing before press forming is performed at an annealing temperature of 790 ° C.
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni of 28.0 kgf / mm ² or less and the degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing a Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a thin alloy plate. 4. A hot rolled sheet having the component composition according to claim 1 is annealed at 910 to 990 ° C., and then subjected to the steps of cold rolling-recrystallization annealing-cold rolling for final re-rolling. Crystal annealing is carried out, and then finish cold rolling is carried out at a rolling ratio R (%) satisfying the following formula according to the average austenite crystal grain size D (μm) after the final recrystallization annealing, and 21 ≦ R ≦ 70 6.38D-122.6 ≦ R ≦ 6.38D-65.2 Next, the softening annealing before press forming is performed at an annealing temperature of 790 ° C.
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni with 27.5 kgf / mm ² or less and a degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing a Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a thin alloy plate. 5. A hot-rolled sheet having the composition of claim 1 is annealed at 910 to 990 ° C. and then subjected to the steps of cold rolling-recrystallization annealing-cold rolling for final re-rolling. Crystal annealing is carried out, and then finish cold rolling is carried out at a rolling ratio R (%) satisfying the following formula according to the average austenite crystal grain size D (μm) after the final recrystallization annealing, and 26 ≦ R ≦ 63 6.38D-108.0 ≦ R ≦ 6.38D-79.3 Next, the softening annealing before press forming is performed at an annealing temperature of 790 ° C.
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni of 27.0 kgf / mm ² or less, and the degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing a Fe-Ni alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a thin alloy plate. 6. A hot-rolled sheet having the composition of claim 2 is annealed at 910 to 990 ° C., and then subjected to the steps of cold rolling-recrystallization annealing-cold rolling for final re-rolling. Crystal annealing is carried out, and then finish cold rolling is carried out at a rolling ratio R (%) satisfying the following formula in accordance with the average austenite crystal grain size D (μm) after the final recrystallization annealing, and 16 ≦ R ≦ 75 6.38D-133.9 ≦ R ≦ 6.38D-51.0 Then, the softening annealing before press forming is performed at an annealing temperature of 790 ° C.
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni of 28.0 kgf / mm ² or less and the degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing an Fe-Ni-Co alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a -Co alloy thin plate. 7. A hot rolled sheet having a composition as set forth in claim 2, after annealing the hot rolled sheet at nine hundred ten to nine hundred and ninety ° C., cold rolling - recrystallization annealing - through the steps of the cold rolling final re Crystal annealing is carried out, and then finish cold rolling is carried out at a rolling ratio R (%) satisfying the following formula according to the average austenite crystal grain size D (μm) after the final recrystallization annealing, and 21 ≦ R ≦ 70 6.38D-122.6 ≦ R ≦ 6.38D-65.2 Next, the softening annealing before press forming is performed at an annealing temperature of 790 ° C.
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni with 27.5 kgf / mm ² or less and a degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing an Fe-Ni-Co alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a -Co alloy thin plate. 8. A hot rolled sheet having the component composition according to claim 2 is annealed at 910 to 990 ° C., and then subjected to the steps of cold rolling-recrystallization annealing-cold rolling for final re-rolling. Crystal annealing is carried out, and then finish cold rolling is carried out at a rolling ratio R (%) satisfying the following formula according to the average austenite crystal grain size D (μm) after the final recrystallization annealing, and 26 ≦ R ≦ 63 6.38D-108.0 ≦ R ≦ 6.38D-79.3 Next, the softening annealing before press forming is performed at an annealing temperature of 790 ° C.
Hereinafter, by performing the annealing time: 40 minutes or less and under the conditions satisfying the following formula, T ≧ −53.8log t + 806 where T: annealing temperature (° C.) t: annealing time (min) 0.2% proof stress Fe-Ni of 27.0 kgf / mm ² or less, and the degree of integration of {211} crystal planes on the plate surface of 16% or less
A method for producing an Fe-Ni-Co alloy thin plate for a shadow mask, which is excellent in press formability, characterized by obtaining a -Co alloy thin plate.