JP2871414B2 - Alloy thin plate for shadow mask excellent in 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 an Fe--Ni--Cr alloy sheet excellent in press formability and an Fe--Ni--Co--
According to a Cr alloy thin plate and a method for producing the same, it is preferable to use Fe-
An object of the present invention is to provide a Ni-Cr alloy thin plate, a Fe-Ni-Co-Cr alloy thin plate, and a method for producing them.

[0002]

2. Description of the Related Art In recent years, in order to cope with the problem of color misregistration with the high quality of color televisions, Fe-Ni based alloys containing 34 to 38 wt% Ni have been used as shadow mask alloys. It has become. This Fe—Ni-based alloy has a significantly lower coefficient of thermal expansion than low carbon steel conventionally used as a material for shadow masks.
If the shadow mask is made of a Ni-based alloy, the problem of color shift due to thermal expansion of the shadow mask is unlikely to occur even if the shadow mask is heated by an electron beam.

An alloy sheet for a shadow mask is generally manufactured by the following steps. That is, an alloy ingot is prepared by a continuous casting method or an ingot-making method, and then the prepared alloy ingot is subjected to slab rolling, hot rolling, cold rolling and annealing to produce an alloy sheet. You do it.

[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, simply referred to as a “hole”) is formed in the alloy thin plate for a shadow mask by photoetching (hereinafter, a thin alloy plate for a shadow mask that has been perforated by etching is referred to as a “flat mask”). Next, the flat mask is annealed, and the annealed flat mask is press-molded into a curved surface shape so as to conform to the shape of a cathode ray tube, and then assembled into a shadow mask, and a blackening process is performed on the surface thereof. Apply.

However, the conventional general Fe-
When a Ni-based alloy is used, this alloy has higher strength and greater in-plane anisotropy of mechanical properties than a conventional low-carbon steel shadow mask, so this alloy is subjected to primary cold rolling.
After recrystallization annealing, the material for the shadow mask obtained by finish rolling is subjected to annealing before pressing after etching perforation, but during subsequent press forming, poor shape freezing, cracking of the material, transmission of light Many troubles such as generation of transmission unevenness occurred, and there was a great inconvenience in the production of cathode ray tubes. Further, the above-mentioned Fe-Ni-based alloy is apt to rust, and in the shadow mask manufacturing process, there is a problem that the rust lowers the product yield.

As a method for reducing the strength of such a conventional Fe-Ni-based alloy material and solving the above-mentioned problems, there is a technique disclosed in Japanese Patent Application Laid-Open No. 3-267320. In this technique, after performing primary cold rolling and subsequent recrystallization annealing, finish cold rolling is performed in a rolling reduction range of 5 to 20%, and subsequently annealing at a temperature of less than 800 ° C. 8. 0.2% proof stress at 200 ° C.
The strength is reduced to 5 kgf / mm ² (10 kgf / mm ² or less), and press formability is improved to a satisfactory level (hereinafter referred to as Prior Art 1).

As a method for reducing in-plane anisotropy, which is a mechanical property of a material, there is the following prior art. That is, in JP-A-64-52024, a method of manufacturing a material for a shadow mask by repeating a combination of the steps of cold rolling and subsequent recrystallization annealing twice or more, and finally performing hardness-added cold rolling. Discloses a technique of obtaining a thick plate for a shadow mask having a small in-plane anisotropy of an elastic coefficient by performing finish cold rolling immediately before a final recrystallization annealing step at a cold rolling reduction of 40 to 80%. I have. When the material is etched and then annealed and press-formed, the deformation of the etching hole is small, and the unevenness of transmitted light gloss and streak-like defects do not occur. (Hereinafter referred to as prior art 2).

[0008]

However, in the prior art 1, under the above-described annealing conditions, the strength is reduced to a level that is favorable for the press formability. It was not enough to satisfy all the molding qualities. That is, the material for the shadow mask according to the above-described technique was liable to seize in the mold during press molding, and cracks were easily generated at the shadow mask end. In addition, the in-plane anisotropy of the material according to this technique is large, and there are often cases where transmission unevenness of light passing through the shadow mask occurs after press molding, which poses a quality problem.

Further, in the above-mentioned prior art 2, the in-plane anisotropy of the elastic coefficient of the material is small, and there is no deformation that causes uneven transmission of transmitted light during press forming. However, this technique also has a problem that a crack is generated at the end of the shadow mask during the press forming described above. Further, there is a problem that the rusting (corrosion resistance) of the Fe—Ni-based alloy has not been improved.

Further, with the recent flattening of the color TV screen for higher brightness and flattening, the required quality with respect to the color shift of the screen has become more severe.
Even in a cathode ray tube using a shadow mask manufactured by the two prior arts, there is a problem that a color misregistration occurs partially when irradiating an electron beam (when using a TV).

The present invention has been made in order to solve the above-mentioned problems of the prior art, and is excellent in corrosion resistance and press formability, and particularly good in compatibility with a mold (a mold). This suppresses the occurrence of cracks during press molding and the occurrence of uneven transmission of transmitted light, and also suppresses the occurrence of partial color shift when the shadow mask is used in a TV. It is an object of the present invention to provide a Ni-Cr alloy thin plate, a Fe-Ni-Co-Cr alloy thin plate, and a method for producing them.

[0012]

According to the first aspect of the present invention, there is provided a thin alloy plate for a shadow mask having excellent press formability, which is expressed by wt%.
And Ni: 34-38%, Cr: 0.05-3.0%,
Si: 0.10% or less, B: 0.0030% or less, O:
0.0030% or less, N: 0.0030% or less, and the average austenite grain size D of the alloy sheet is 15 to 4
An Fe-Ni-Cr alloy thin plate having an austenite grain size of 5 µm and a mixed grain size K of 50% or less determined by Equation 6 and having a degree of crystal plane integration on the alloy plate surface satisfying the values shown in Table 4.

[0013]

(Equation 6)

Where K: mixed grain size of austenite crystals (%) D: average austenite grain size in alloy plate D _max : maximum austenite grain size in alloy plate

[0015]

[Table 4]

The second thin alloy sheet for a shadow mask having excellent press formability according to the present invention is Ni:
34-38%, Cr: 0.05-3.0%, Co: 1.
0% or less, Si: 0.10% or less, B: 0.0030%
In the following, O: 0.0030% or less, N: 0.0030% or less, the average austenite crystal grain size D of the alloy plate is 15 to 45 μm, and the mixed grain size K of the austenite crystal grains determined by Equation 7 is 50% or less. And the degree of crystal plane integration on the surface of the alloy plate satisfies the values shown in Table 5.
It is an r-Co alloy thin plate.

[0017]

(Equation 7)

K: mixed grain size of austenite crystals (%) D: average austenite grain size in alloy plate D _max : maximum austenite grain size in alloy plate

[0019]

[Table 5]

Further, the third thin alloy sheet for shadow masks having excellent press formability according to the present invention is Ni:
27-38%, Cr: 0.05-3.0%, Co: 1.
0% to 7%, Si: 0.10% or less, B: 0.0
030% or less, O: 0.0030% or less, N: 0.00
30% or less, the average austenite crystal grain size D of the alloy sheet is 15 to 45 μm, the mixed grain size K of the austenite crystal grains determined by Equation 8 is 50% or less, and the degree of crystal plane integration on the surface of the alloy sheet Satisfying the values shown in Table 6
Ni-Cr-Co alloy thin plate.

[0021]

(Equation 8)

K: mixed grain size of austenite crystal (%) D: average austenite crystal grain size in alloy plate D _max : maximum austenite crystal grain size in alloy plate

[0023]

[Table 6]

Further, the first method for producing an alloy sheet for a shadow mask excellent in press formability according to the present invention is a hot rolled steel alloy having the same composition as the first, second or third alloy sheet. After hot strip strip annealing, the first cold rolling and subsequent recrystallization annealing are performed, followed by finish cold rolling and strain relief annealing to provide a shadow press alloy with excellent press formability. When manufacturing a thin sheet, the hot-rolled sheet annealing is performed at 810 to 890 ° C., and the reduction rate in the first cold rolling is 81 to 94%, and the reduction rate in the finish cold rolling is 14 to 29.
%, And then, before press forming, the alloy sheet is annealed under the conditions that the annealing temperature is 740 to 900 ° C., the annealing time is 2 to 40 minutes, and the annealing time T satisfies Expression 9. The average grain size of austenite, the mixed grain size of austenite crystal grains, and the degree of integration of crystal planes on the surface of the alloy sheet are set in the same ranges as those of the first, second or third alloy sheet.

[0025]

(Equation 9)

Here, T: annealing temperature (° C.) t: annealing time (minute)

Further, the second method for producing an alloy sheet for a shadow mask having excellent press formability according to the present invention is directed to a hot-rolled steel alloy having the same components as the first, second or third alloy sheet. After the strip is hot-rolled and annealed, it is subjected to primary cold rolling and subsequent primary recrystallization annealing, and then to secondary cold rolling and subsequent secondary recrystallization annealing, followed by finish cold rolling. By performing the strain relief annealing, when producing an alloy sheet for a shadow mask excellent in press formability, the hot-rolled sheet annealing is performed at 810 to 890 ° C., and the rolling reduction in the first cold rolling is 40 to 55%, the rolling reduction in the secondary cold rolling is 81 to 94
%, And the rolling reduction in the finish cold rolling is in the range of 14 to 29%, respectively.
0 to 900 ° C., annealing time 2 to 40 minutes, and annealing temperature T
Annealing under the condition that satisfies several tens, the average austenite crystal grain size of the alloy thin plate, the mixed grain size of the austenite crystal grains and the degree of integration of the crystal plane on the alloy plate surface are controlled by the first, second, or third In the same range as the alloy thin plate.

[0028]

(Equation 10)

Here, T: annealing temperature (° C.) t: annealing time (minute)

[0030]

The present invention as described above will be further described. From the above-mentioned viewpoint, the present inventors have found that shadows excellent in press moldability and capable of suppressing the occurrence of partial color misregistration when used in a color television are provided. As a result of intensive studies to develop Fe-Ni-Cr alloy thin plates and Fe-Ni-Co-Cr alloy thin plates for masks, the following findings were obtained. That is,
Fe-Ni-Cr alloy sheet for shadow mask and Fe
-By adjusting the chemical composition of the Ni-Co-Cr alloy sheet, the austenitic crystal grain size and its mixed grain size, and the crystal orientation within a predetermined range, the required press-forming quality is imparted, and It is possible to suppress the occurrence of the partial color shift.

More specifically, by restricting the contents of B and O within a predetermined range, the growth of crystal grains during annealing before pressing under the conditions characteristic of the present invention is improved, and the predetermined austenite crystal is formed. By giving the particle size, shape freezing property at the time of press molding is imparted, and by limiting the content of Si and N within a predetermined range, the conformity with the mold at the time of press molding is improved (to the mold). The occurrence of galling) is suppressed, and the degree of integration of the {211} crystal plane on the surface of the alloy sheet after pre-press annealing is within a predetermined range, thereby suppressing the occurrence of cracks in the material during press forming.

Further, by setting the mixed grain size of the austenite crystal grains after the pre-press annealing to within a predetermined range, the occurrence of transmission unevenness at the time of press forming is suppressed, and the surface roughness of the alloy sheet after the pre-press annealing is reduced. By setting the degree of integration of the 210 ° and {331} crystal planes within a predetermined range, the above-described partial color shift is suppressed from occurring.

Further, the present inventors have obtained the following findings. That is, in the production process of the present alloy, a hot-rolled sheet strip is annealed at a predetermined temperature before cold-rolling the hot-rolled steel strip, and the cold-rolling rate and the final cold-rolling rate before and after the cold rolling are performed in the subsequent cold rolling. By setting the annealing conditions (temperature, time) of
Average austenite grain size of alloy sheet after pre-press annealing and {331}, {210}, {2}
The degree of integration of the 11 crystal plane can be adjusted within a predetermined range ({331}, {210}, {2
The {11} crystal plane integration degree is simply referred to as {331}, {21}
0} and {211} crystal planes, respectively.)

Further, in order to keep the mixed grain size of austenite crystal grains in the alloy sheet after annealing before press within a predetermined range, the rolling reduction in one or two times of cold rolling after annealing of the hot-rolled sheet is set to a predetermined value. It is particularly important to be within the range.

The present invention has been made based on the above-described findings, and the Fe for shadow mask according to the present invention has been developed.
-Chemical composition of Ni-Cr alloy thin plate and Fe-Ni-Co-Cr alloy thin plate, austenite crystal grain size after annealing before press and its mixed grain size, and # 33 on the alloy sheet surface
The reason for limiting the degree of integration of {1}, {210}, and {211} crystal planes within the above range is as follows.

(1) Ni In order to prevent the occurrence of color shift, Fe
The upper limit of the average thermal expansion coefficient in the temperature range of 30 ° C. to 100 ° C. required for the Ni alloy sheet is 2.0 × 10 ^−6.
/ ° C. The coefficient of thermal expansion depends on the nickel content of the alloy sheet. The range of the Ni content that satisfies the above-mentioned condition of the average thermal expansion coefficient is in the range of 34 to 38 wt%. Therefore, the Ni content should be limited within the range of 34-38 wt%. In addition, even within such a range of the Ni content, a preferable Ni amount that can reduce the average thermal expansion coefficient is 35 to 37%, and a more preferable Ni amount that can further reduce the average thermal expansion coefficient is 35. .5
３６36.5%.

Even when Co is contained in an amount of 0.001 to 1.0%, the Ni value satisfying the upper limit of the average thermal expansion coefficient is 34 to 38%. Even in such a case, the preferable amount of Ni that can reduce the average thermal expansion coefficient is 35 to 3
8%. When Co is contained in an amount of more than 1.0% and up to 7%, Ni that satisfies the above condition of the average thermal expansion coefficient is used.
The range of amounts is 27-38%, and Fe-Ni-C
In o-Cr and Fe-Ni-Cr alloys, N
By setting the i content to 30 to 33% and the Co content to 3 to 6%, the average coefficient of thermal expansion becomes even lower and the product becomes excellent.

Cr is an element that improves the corrosion resistance of the present alloy but deteriorates (increases) the coefficient of thermal expansion. Cr is 0.
If it is less than 05%, the effect of improving corrosion resistance cannot be obtained, while if it exceeds 3.0%, the average thermal expansion coefficient intended in the present invention cannot be obtained.
It was determined to be 5% and 3.0%.

In the present invention, the average austenite particle size required for improving the shape freezing property at the time of press forming, suppressing the occurrence of cracks in the alloy sheet, and preventing the occurrence of transmission unevenness after press forming is determined by the warm pressing method. Assuming that
４５45 μm. If the thickness is less than 15 μm, the shape freezing property is poor, and cracks of the alloy plate also occur. On the other hand, if it exceeds 45 μm, cracks occur, and transmission unevenness occurs after press forming. From the above, the average austenite particle size was determined to be 15 to 45 μm.

In order to suppress the occurrence of cracks in the material, the degree of integration of {211} crystal planes on the surface of the alloy plate is suppressed to a specific value while having the above average austenite grain size as described later. It is essential. However, in order to enhance the growth of crystal grains under the pre-press annealing conditions intended in the present invention, in order to suppress O and B to a specific value or less, and to improve the familiarity of the mold during press forming, , Si, and N need to be suppressed to specific values or less, respectively.
It is as follows.

(2) O 2 O (oxygen) is one of the impurities unavoidably mixed into the alloy.
One. When the content of O increases, the amount of oxide-based nonmetallic inclusions in the alloy increases, and when this inclusion is annealed before press forming particularly at an annealing temperature of 740 to 900 ° C. and an annealing time of 40 minutes or less. Inhibits the growth of crystal grains. That is, when the O content exceeds 0.0030%, the above-described effect of inhibiting the grain growth becomes remarkable, and the austenite crystal grain size intended in the present invention cannot be obtained.

(3) BB B improves hot workability in the present alloy, but when the content is large, it segregates at the grain boundaries of recrystallized grains formed at the time of annealing before pressing, and forms the grain boundaries. As a result, the growth of crystal grains is hindered, and a required austenite crystal grain size 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 grain growth is strong, and this effect does not work uniformly for all crystal grains, and as a result, the effect is remarkable. It shows a mixed grain structure and causes unevenness in elongation of the material during press forming, which causes transmission unevenness.

In addition, B increases the degree of integration of {211} crystal planes that cause cracks in the material skirt after annealing. If the B content exceeds 0.0030%, the above-mentioned effect of inhibiting grain growth becomes remarkable, and the austenite crystal grain size intended in the present invention cannot be obtained, and problems such as transmission unevenness during pressing also occur. Further, the degree of integration of the {211} crystal plane also exceeds the upper limit specified in the present invention. From the above, the upper limit of the B content is determined to be 0.0030%.

(4) Si Si is used as a deoxidizing element when the present alloy is melted. If it exceeds 0.10%, an oxide film of Si is formed on the surface of the alloy during annealing before pressing. The oxide film deteriorates the compatibility with the mold at the time of press molding, and causes the alloy to bite the mold. Therefore, the upper limit of the amount of Si was set to 0.10%. Even if the content of Si is 0.10% or less, the familiarity between the alloy plate and the mold can be further improved by further reducing the amount of Si.

(5) N N is an element that is inevitably mixed during the melting of the present alloy. If it exceeds 0.0030%, N is concentrated on the alloy surface during annealing before pressing, and the N The nitride deteriorates the compatibility with the mold at the time of press molding, and causes the alloy to bite the mold. Therefore, the upper limit of N content is 0.0030%
It was decided.

The alloy for a shadow mask according to the present invention comprises an Fe--Ni alloy and an Fe--Ni--
A specific amount of O, N, Si, N is allowed in the basic composition of the Co alloy, and the average austenite grain size after annealing before pressing is 15 to 45 μm, and the mixed grain size of austenite grains is 30% or less. Then, {211}, {331}, {21
The feature is that the degree of integration of the 0 ° crystal plane is set to 20% or less, 35% or less, and 16% or less, respectively. In addition to the above-mentioned composition, C: 0.0001 to 0.0040%, Mn:
0.001 to 0.35%, Cr: 0.001% to 0.0
It is preferable to contain H within the range of 5% and H: 2.0 ppm or less.

By controlling the components and setting the average austenite crystal grain size after annealing before press within the provisions of the present invention as described above, galling of the present alloy into a mold during press forming is suppressed, and the shape of the alloy is reduced. Although the freezing property can be set at an excellent level, cracking of the material still poses a problem in press molding quality. Thus, the present inventors
In order to solve such a problem, the relationship between the components within the range of the present invention and the crystal orientation of the present alloy sheet having the average austenite crystal grain size was changed variously, and the relationship with the material cracking during press forming was examined. As a result, in order to suppress cracking of the present alloy material, it is effective to suppress the degree of integration of {211} crystal planes to a specific value or less, in addition to defining the average austenite crystal grain size after annealing before pressing. I found that.

FIG. 1 shows the relationship between alloy cracks during press forming, the degree of integration of {211} crystal planes, and the average austenite crystal grain size for alloy sheets having components characteristic of the present invention. 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 (111), (200), (220), and (31).
1), (331), (420), and (422) were obtained by dividing by the sum of the relative X-ray intensity ratios of the respective diffraction surfaces. When measuring the degree of {211} crystal plane integration, it is measured by diffraction of a (422) plane which is azimuthally the same as this crystal plane.

Here, the relative 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 surface is obtained by dividing the X-ray diffraction intensity of the (111) diffraction surface by the theoretical X-ray diffraction intensity of the (111) diffraction surface. The measurement of the degree of integration of the {331} and {210} crystal planes, which will be described later, is performed on the (331) diffraction plane and the (42) diffraction plane, respectively.
1) Relative X-ray diffraction of the seven diffraction planes (111) to (422) of the relative X-ray diffraction intensity ratio of the diffraction plane (which is equivalent to the {210} crystal plane in terms of valence) It is determined by dividing by the sum of the intensity ratios.

As shown in FIG. 1, the average austenite grain size is 15 to 45 μm and the degree of integration of the {211} crystal plane is 20% or less. Therefore, the excellent effects intended in the present invention are exhibited.

From the above examination results, the degree of integration of the {211} crystal plane was determined to be 20% or less as a condition for suppressing cracking of the alloy sheet.

The control of the mixed grain size of the austenite crystal grains after the pre-press annealing is necessary to prevent the occurrence of transmission unevenness during press forming. FIG. 2 shows components within the scope of the present invention,
Average austenite grain size, {331}, # 21
Using an alloy plate having a degree of integration of {0} and {211} crystal planes, the relationship between the occurrence rate of transmission unevenness after press forming and the mixed grain size of austenite crystal grains was examined. From this figure, it can be seen that when the mixed particle size of the austenite crystal grains exceeds 50%, the occurrence rate of transmission unevenness increases. As described above, in order to prevent the occurrence of transmission unevenness after press molding, the range of the mixed particle size of austenite crystal grains is set to 50% or less.

As described above, the O, B,
The press forming quality intended in the present invention can be made excellent by the provisions of Si and N and the provision of the mixed grain size of austenite crystal grains after annealing before pressing and the degree of integration of {211} crystal planes.

In order to suppress the occurrence of the partial color shift as described above, it is necessary to suppress the degree of integration of the {331} crystal plane and the {210} crystal plane after annealing before pressing. That is, {331} crystal plane after annealing before press,
When the degree of integration of the {210} crystal plane exceeds 35% and 20%, partial color shift occurs. Therefore, in the present invention, the degree of integration of the {331} and {210} crystal planes is determined to be 35% or less and 20% or less, respectively.

{331} 21 after annealing before press
0%, {211} crystal plane integration degree is 35% or less,
In order to reduce the content to 20% or less, in the process from solidification of the alloy to hot working and in the subsequent cold rolling and annealing steps, the {331} 210} and {211} crystal planes are not accumulated as much as possible. It is necessary. For example, when producing a slab obtained by ingot-bulking rolling or a continuously cast slab of the present alloy from a hot-rolled steel strip obtained by hot rolling, the hot-rolled steel strip is used as a material. After that, a hot-rolled sheet annealing-cold rolling-recrystallization annealing-finishing cold rolling-strain relief annealing is performed, then annealing before press forming is performed, and a black masking process is performed after press forming. In this case, appropriate hot-rolled sheet annealing is first performed after hot rolling in the case of {331} 21.
This is effective for preventing the {0} and {211} crystal planes from being accumulated. At this time, the temperature of the hot-rolled sheet annealing is {331} 21 if an appropriate temperature is selected in the range of 810 to 890 ° C.
The degree of integration of the {0} and {211} crystal planes can be set to the values specified in the present invention, respectively.

As described above, the degree of integration of the {331} crystal plane is 35% or less, and the degree of integration of the {210} crystal plane is 20%.
Hereinafter, the annealing temperature of the hot rolled sheet is set at 810 to 890 ° C. in order to set the degree of integration of the {211} crystal plane to 20% or less.

In the present invention, such hot-rolled sheet annealing is performed 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 integration of the {331} 210} and {211} crystal planes intended in the present invention, in producing the present alloy, the slag homogenizing heat treatment after slab rolling is not preferable. For example, when the above-mentioned uniform heat treatment is performed at a temperature of 1200 ° C. or more and a processing time of 10 hours or more, {331 {210};
Such processing must be avoided since one or more of the {211} crystal plane integration degrees exceed the prescribed value of the present invention.

In the case of manufacturing from the above-mentioned hot-rolled steel strip, the intermediate cold rolling / annealing conditions, the final cold rolling conditions, the strain relief annealing conditions, and the pre-press annealing conditions in the above-described series of steps are used. The optimization is also {331} 210}, {211}
It is necessary to keep the degree of integration of the crystal planes below the specified value of the present invention and to obtain a mixed grain size of austenite crystal grains within the range of the present invention. After the hot-rolled sheet annealing, it is important to optimize the intermediate cold rolling and annealing conditions in order to control the mixed grain size of the austenite crystal grains after the pre-press annealing.

FIG. 3 shows the cold rolling ratio and the mixed grain size of the austenite crystal grains after the pre-press annealing when the number of times of the intermediate cold rolling and annealing after the hot-rolled sheet annealing was one when the alloy of the present invention was used. It shows the relationship. That is, the hot-rolled steel strip is
Hot rolled sheet annealing at 90 ° C., then primary cold rolling is performed in the range of 73 to 97% of the cold rolling rate to perform recrystallization annealing, and then finish cold working at the cold rolling rate of 14 to 29%. Rolling,
At a temperature of 450 to 540 ° C., the strain relief annealing is performed over a time of 0.5 to 300 seconds, and finally, before press molding, the annealing temperature is 740 to 900 ° C., and the annealing time is 2 to 40 minutes, FIG. 9 is a graph in which the mixed grain size of austenite crystal grains of an alloy thin plate annealed under the condition that the annealing time T satisfies Formula 11 is arranged in relation to the primary cold rolling reduction.

[0060]

[Equation 11]

As is apparent from FIG. 3, when the intermediate cold rolling annealing process is performed once, the mixed grain size of austenite crystal grains is 50% or less and within the scope of the present invention when the cold rolling rate is 8%.
It is in the range of 1-94%. On the other hand, when the cold rolling reduction is less than 81% or more than 94%, the mixed particle size exceeds 50%. From these facts, when the intermediate cold-rolling annealing process is performed once, the cold-rolling ratio is set to 81 to reduce the mixed particle size to 50% or less.
It was determined to be 94%.

FIG. 4 is a graph showing the relationship between the cold rolling ratio and the mixed grain size of austenite crystal grains when the number of times of intermediate cold rolling and annealing is two when the alloy of the present invention is used. That is, the hot-rolled steel strip is annealed at 810 to 890 ° C., then the first cold rolling is performed in the range of 35 to 60% of the cold rolling rate to perform recrystallization annealing, and then the second cold rolling is performed. Rolling is performed in the range of 75-97% of the cold rolling ratio to perform recrystallization annealing, and then performing finish cold rolling at the cold rolling ratio of 14-29%,
At a temperature of 450 to 540 ° C., the strain relief annealing is performed over a time of 0.5 to 300 seconds, and finally, before press molding, the annealing temperature is 740 to 900 ° C., and the annealing time is 2 to 40 minutes, FIG. 4 is a graph in which the mixed grain size of austenite crystal grains of an alloy sheet annealed under the condition that the annealing time T satisfies Expression 12 is arranged in relation to the primary cold rolling ratio and the secondary cold rolling ratio.

[0063]

(Equation 12)

As is apparent from this figure, the secondary cold rolling reduction is in the range of 81 to 94% and the primary cold rolling reduction is 40 to 55.
%, The mixed particle size shows a better value.

As described above, when the cold rolling annealing process is performed twice, the primary cold rolling reduction is 40 to 55%, and the secondary cold rolling reduction is 81 to 9
It was set at 4%. The recrystallization annealing after the first and second cold rolling is preferably performed at an annealing temperature of 810 to 840 ° C. and an annealing time of 0.5 to 3 minutes. Even if the annealing temperature is equal to or higher than the recrystallization temperature, the mixed grain structure is exhibited in annealing at 810 ° C. or lower, so that the mixed grain size of the austenite crystal grains is increased even after annealing before pressing. Further, even in the range of 810 to 840 ° C., a mixed grain structure is obtained when annealing is performed for less than 0.5 minutes, and a mixed grain structure is obtained when annealing is performed for more than 3 minutes. It is not preferable because it becomes high. When the cold rolling / annealing conditions within the range of the present invention described above are adopted, {331 {210}, {21}
The degree of integration of the 1｝ crystal plane is 35% or less, 20% or less, and 20% or less, respectively.

When the finish cold-rolling ratio is in the range of 14 to 29%, if the components, cold-rolling / annealing conditions and annealing conditions before press forming are adopted within the range of the present invention, after the annealing before press forming, The average austenite grain size is 15-45μ
m, mixed particle size of austenite crystal grains is 50% or less, # 3
The degree of integration of the {31} crystal plane ≦ 35%, the degree of integration of the {210} crystal plane ≦ 20%, and the degree of integration of the {211} crystal plane ≦ 20%. On the other hand, when the finish cold rolling reduction is less than 14% or more than 29%, one or more of the above-mentioned respective characteristics of the present invention do not satisfy the scope of the present invention. Therefore, the finish cold rolling rate is 1
4 to 29%.

In the present invention, in order to keep the average austenite crystal grain size and the mixed grain size of austenite crystal grains within the range of the present invention, it is also important to optimize annealing conditions before pressing. Fig. 5 shows the average austenite grain size after annealing before pressing, and the mixed grain size of austenite grains of alloy sheets whose components, hot-rolled sheet annealing conditions, intermediate cold-rolling / annealing conditions, and finish cold rolling ratio are within the range of the present invention. , {331}, $ 21
4 is a graph showing the relationship between the degree of integration of {0} and {211} crystal planes, the pre-press annealing temperature (T, ° C.), and the time (t, minute).

As is apparent from FIG. 5, even if conditions other than the pre-press annealing conditions are within the scope of the present invention, the annealing temperature T
Is T <−123 logt + 937, the average austenite grain size is less than 15 μm, and {211}
The degree of integration of the crystal plane exceeds 20%, which is not suitable. When the annealing temperature T exceeds 900 ° C., the average austenite crystal grain size exceeds 45 μm and the degree of integration of the {211} crystal plane is 2
When the annealing time t exceeds 40 minutes, one or more of {211}, {331}, and {210} crystal planes are more than the present invention. It is not suitable because it accumulates.

As described above, the average austenite grain size, the mixed grain size of austenite grains, and
The conditions for obtaining the degree of integration of the {31}, {210}, and {211} crystal planes are as follows: annealing temperature T is 740 to 900 ° C., annealing time t is 2 to 40 minutes, and the relationship between annealing temperature T and annealing time t is , T ≧ −123 logt + 937. In addition, the strain relief annealing performed in the present invention is {331}, {210}, {211} in the pre-press annealing performed thereafter.
It is important for controlling the degree of integration of crystal planes, and the conditions for strain relief annealing for sufficiently exhibiting the effect intended in the present invention are as follows: annealing temperature is 450 to 540 ° C .;
300 seconds.

The method of controlling the degree of integration of {331}, {210}, and {211} crystal planes in the present alloy thin sheet after annealing before press forming to within the prescribed range of the present invention is the same as that of the rapid solidification method described above. There is a texture control by adoption and control of recrystallization in hot working. 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 range specified in the present invention, required photo-etching quality can be ensured.

[0071]

The present invention as described above will be described in more detail with reference to specific examples. (Example 1) First, the present inventors prepared an alloy No. having the chemical components shown in Table 7 below from molten steel refined by ladle refining. 1 to No. 21 CC slabs were each manufactured by a continuous casting method.

[0072]

[Table 7]

After cleaning the surface flaws of the CC slab, the CC slab was heated in a heating furnace at 1100 ° C. for 3 hours.
It was hot rolled into a hot rolled steel strip. 860 ℃
After hot-rolled sheet annealing, primary cold rolling at a cold rolling reduction of 93% was performed, followed by recrystallization annealing at 810 ° C. for 1 minute. Then, after performing finish cold rolling at a cold rolling reduction of 21%, strain relief annealing was performed at 530 ° C. for 1 second to obtain an alloy thin plate having a thickness of 0.25 mm. Various investigations described below were conducted using the alloy thin plate thus obtained as a test material. Is the above alloy No. 1 to N
o. 21 corresponding to the material No. 21 respectively. 1 to No. 2
It was set to 1. The hot-rolled steel strip described above was selected from those which had sufficiently recrystallized after hot rolling.

Each of the obtained material Nos. 1 to No. 21 among material Nos. 1 to No. 3, No. 5-No. After flattening each alloy plate of No. 21 by etching, these flat masks were annealed before pressing under the conditions shown in Table 8 and then press-formed to obtain a shape freezing property, conformity with a mold, and material The frequency of occurrence of cracks and transmission unevenness was examined according to the evaluation criteria shown in Table 10 below. The corrosion resistance of each material was also evaluated by the evaluation method shown in Table 10 after the stress relief annealing.

[0075]

[Table 8]

It is confirmed that the flat mask after the above-mentioned etching has no unevenness and has the required etching performance. And after annealing before press of each material,
Average austenite crystal grain size and its mixed grain size, tensile properties (n value, r value, elongation value) and {331}, {21}
The degree of integration of the {0} and {211} crystal planes was investigated. This $ 3
The measurement of the degree of integration of the 31 °, {210}, and {211} crystal planes was determined by the above-described X-ray diffraction method. Table 9 shows the results.

[0077]

[Table 9]

The material No. The alloy plate of No. 4 was subjected to pre-press annealing under the conditions shown in Table 8 after the strain relief annealing under the above conditions, followed by etching to form a flat mask, and then press forming. Each characteristic value of this material is examined in the same manner as the other materials described above. The occurrence of partial color misregistration was examined after the press-molded shadow mask was blackened, assembled into a Braun tube, and irradiated with an electron beam for a predetermined time. Table 10 shows the press forming quality (shape freezing property, conformity with the mold, occurrence of cracks in the alloy sheet, occurrence of transmission unevenness), presence / absence of partial color shift occurrence, and corrosion resistance (frequency of rust spot occurrence, pieces / 100 cm ^2). ) Shows the results of the survey.

[0079]

[Table 10]

As is apparent from Table 10, the composition of the present invention has a composition within the range of the present invention, and is within the range of the present invention.
The degree of integration of 1｝, {210｝, and {211} crystal planes;
Material No. having an average austenite crystal grain size and a mixed grain size of austenite crystal grains. 1 to No. 13, No.
Each of the materials No. 13-1 has an excellent level of press molding quality, has no partial color shift, and has a corrosion resistance of Material No. 16 compared to 16. Note that N
o. Material No. 4 was etched after annealing before pressing, but the flat mask had no unevenness and had the required etching performance. N with much Co
o. The 13-1 steel also shows excellent properties.

On the other hand, the material No. No. 14 has a Si content of 0.12%. No. 16 is a case where the content of N exceeds 0.0035% and exceeds the regulation of the present invention;
There is a problem with the familiarity with the mold. Material No. 15 is O
Is in excess of the prescribed value of the present invention of 0.0035%, the average austenite crystal grain size is 13 μm, which is less than the prescribed range of the present invention (hereinafter simply referred to as the average particle size), and the shape freezing property is poor. , Cracks in the alloy plate have also occurred,
Further, the mixed particle size of austenite crystal grains (hereinafter, simply referred to as mixed particle size) is 60%, which exceeds the value specified in the present invention, and transmission unevenness occurs, which causes a problem in press molding quality. In addition, material No. The sample No. 16 to which Cr was not added has the corrosion resistance described above (Material No. 1 to No. 1).
3, No. It is significantly inferior to 13-1).

The material No. 17 has a B content of 0.0
035% and material No. 18 has an O content of 0.0
In this case, the average particle diameter is 12 μm and 14 μm, respectively, which is less than the lower limit of 15 μm specified in the present invention, and the shape freezing property is inferior. Furthermore, the mixed particle size of these materials was 56% and 63%, respectively.
Exceeds the upper limit of 50% specified in the present invention, and transmission unevenness also occurs. Also, the degree of integration of the {211} crystal plane is 30% and 34%, respectively, which is the upper limit of 20 according to the present invention.
%, The alloy sheet cracks, and there is a problem in press forming quality.

Further, the material No. In No. 19, the degree of integration of the {210} crystal plane was 21%, exceeding the upper limit of 20% specified in the present invention. No. 20 is the case where the degree of integration of the {331} crystal plane is 38%, which exceeds the upper limit of 35% specified in the present invention. Partial color shift occurs, and there is a problem in screen quality. In addition, material No. 21 has an average particle size of 52 μm
And exceeds the upper limit of 45 μm specified in the present invention,
Cracking of the alloy plate has also occurred, and transmission unevenness has also occurred, and there is a problem in press molding quality. In this case,
The degree of integration of the {211} crystal plane is also 23%, exceeding the upper limit of 20% specified in the present invention, and the crystal orientation is 920 ° C. × 4.
Under the annealing condition before press of 0 minute, it is recognized that the degree of accumulation is increased as the average particle diameter is increased.

As is apparent from the above description, the component composition within the scope of the present invention and $ 33 within the scope of the present invention
The degree of integration of 1｝, {210｝, and {211} crystal planes;
By the average particle size and the mixed particle size, the press molding quality and screen quality intended in the present invention have an excellent level,
It is clear that an Fe—Ni-based alloy sheet and an Fe—Ni—Co-based alloy sheet for a shadow mask having excellent corrosion resistance can be obtained.

(Example 2) The alloy No. used in Example 1 was used. 1 to No. 13, No. The hot-rolled steel strip of No. 13-1 was subjected to hot-rolled sheet annealing under the temperature conditions shown in Table 11, and then cold-rolled at the cold-rolling rate shown in Table 11 (CR ₁ had no numerical value. It means that cold rolling was performed once at the cold rolling rate described in _{2. The} one having a numerical value in both CR ₁ and CR ₂ means that cold rolling was performed twice at the cold rolling rate described in each case. After cold rolling, each was subjected to recrystallization annealing at 810 ° C. for 1 minute, and subsequently, as shown in Table 1.
Finish cold rolling was performed at the cold rolling rate shown in FIG.
(30 ° C. × 0.5 seconds) to obtain alloy plates (Material Nos. 22 to 47) each having a thickness of 0.25 mm.

[0086]

[Table 11]

Of these materials, 22-No. 3
9, No. 41-No. 42, No. 44-No. 47
After making an alloy plate into a flat mask by etching,
The flat mask was subjected to pre-press annealing under the conditions shown in Table 11, followed by press molding, and the press molding quality and partial color shift occurrence shown in Table 13 were examined. Table 12 shows the results.

[0088]

[Table 12]

Prior to these investigations, the average austenite grain size of each material, the degree of austenite crystal flow mixing, the degree of integration of {331}, {210}, and {211} crystal planes and the mechanical properties (n Value, r value, elongation) were investigated. Table 13 shows the results.

[0090]

[Table 13]

The flat mask after the above-mentioned etching had no unevenness, and it was confirmed that it had the required etching performance. In addition, No. 40 and no. The alloy plate of No. 43 was subjected to pre-press annealing under the conditions shown in Table 11 after the strain relief annealing under the above conditions, followed by etching to form a flat mask, and then press forming. Each characteristic value of this material is also examined in the same manner as the other materials described above.

As is clear from Tables 12 and 13, the composition of the present invention is within the range of the present invention, and the conditions of hot-rolled sheet annealing, primary and secondary cold rolling rates, finishing cold-rolling rates, and pre-press annealing conditions ( (Annealing temperature and annealing time) are within the range specified by the present invention, and have the degree of integration of {331}, {210}, and {211} crystal planes, the average grain size, and the mixed grain size within the range of the present invention. Material No.
31-No. Each material of No. 47 shows excellent press molding quality, and there is no partial color shift. In addition, No. 40
And No. 43 was etched after annealing before pressing, but the flat mask had no unevenness and had the required etching performance.

No. containing Co. 47 materials also show excellent properties. Also, among the above-described invention examples,
Material No. 32, no. 35-No. 37, no. 3
9, No. 43-No. 45, no. Each material of No. 47 is a case where cold rolling is performed twice, and when the first cold rolling rate (CR ₁ ) is in the range of 40 to 55%, the mixed particle size becomes one. Only by cold rolling (material N
o. 31, No. 33-No. 34, no. 38, N
o. 40-No. 42, No. It can be seen that a lower and preferable level is shown as compared with the case of 46).

On the other hand, the material No. In No. 22, the hot-rolled sheet annealing temperature was 800 ° C., which is lower than the lower limit of 810 ° C. specified in the present invention. 23 shows that the hot-rolled sheet annealing temperature is 90
0 ° C, which exceeds the lower limit of the specification of the present invention, and the degree of integration of the {210} and {211} crystal planes respectively exceeds the upper limit of the present invention. In the latter case, cracks of the alloy plate also occur, and there are problems in screen quality and press molding quality, respectively.

Material No. No. 24 has a cold rolling reduction in the first cold rolling of 95%, which exceeds the upper limit of 94% specified in the present invention. In No. 25, the cold rolling reduction in the single cold rolling is 80%, which is less than the upper and lower limits of 81% specified in the present invention, and the mixed particle size is 59% and 55%, which exceeds the specified value of the present invention. , Transmission unevenness occurs, and there is a problem in press molding quality.

Further, the material No. Reference numeral 26 denotes a finish rolling reduction in single cold rolling of 40%, which is the upper limit value 29 according to the present invention.
%, And the material No. No. 27 indicates that the finish cold rolling rate in single cold rolling is 12%, which is lower than the lower limit of 14% specified in the present invention. The former has an average particle size of 1
3 μm, which is less than the prescribed lower limit of 15 μm of the present invention, there is a problem in the shape freezing property, and cracks of the alloy plate have occurred.
The latter has a mixed particle size of 60%, which is the upper limit of 50 according to the present invention.
%, And transmission unevenness has occurred. Furthermore,
The degree of integration of the {211} crystal plane is 23%, which exceeds the upper limit of 20% specified in the present invention, cracking of the alloy plate occurs, and the degree of integration of the {210} crystal plane is defined by the present invention. (Table 13 and 18% in Table 10 in the proposal)
And does not exceed the upper limit), and partial color misregistration has occurred.

Material No. Material No. 28 has a pre-press annealing temperature of 920 ° C., which exceeds the upper limit of 900 ° C. of the present invention. Reference numeral 29 denotes a pre-press annealing time of 5 hours.
0 minutes and exceeding the prescribed upper limit value of 40 minutes of the present invention,
Material No. In the case of No. 30, the annealing temperature T is (−123 logt + 9).
37) is not satisfied. Material No. 28
Has an average particle diameter of 48 μm and an upper limit of 45 μm specified in the present invention.
m, and transmission unevenness has occurred. Also, {211}
The degree of integration of crystal planes is 25%, which is the upper limit of 20% according to the present invention.
, And cracks of the alloy plate have also occurred.

Material No. In No. 29, the degree of integration of the {331} crystal plane is 38%, which exceeds the upper limit of 35% specified in the present invention, and the alloy plate cracks and a partial color shift occurs.

Further, the material No. 30 means that the average particle size is 13
μm, which is less than the lower limit of 15 μm specified by the present invention, there is a problem in shape freezing properties, and the degree of integration of {211} crystal planes is 26%, exceeding the upper limit of 20% specified by the present invention. Also, cracks of the alloy plate have occurred.

As described above, even when the component composition falls within the range of the present invention, the hot rolled sheet annealing condition, the cold rolling condition, the finish cold rolling rate, and the pre-press annealing condition are set within the range of the present invention. It is understood that the press molding quality and screen quality intended in the present invention can be obtained.

Further, the material No. in the above-described embodiment was used.
4, no. 40, no. 43, Fe-Ni-Cr-based alloy sheets and Fe-Ni-Co-Cr-based alloy sheets having the required press forming quality characterized by the present invention and having no partial color shift. It can be understood that the obtained flat mask has no unevenness even when is etched, and the required etching property is obtained.

As is clear from the above Examples 1 and 2, when the degree of integration of the {211} crystal plane exceeds 20% and / or the average crystal grain size is out of the range of the present invention, before pressing. Elongation after annealing, n value, r value is lower than that of the present invention,
When the degree of integration of the {211} crystal plane is high, or when the average particle size is out of a specific range or at least one of the states, these specific values are reduced, and cracks occur during press molding. It is estimated that.

[0103]

According to the present invention as described in detail above,
Excellent press moldability, that is, excellent shape freezing during molding and compatibility with good molds, suppression of cracking of materials, suppression of transmission unevenness, and further suppression of partial color shift occurrence Fe-Ni-Cr alloy thin plate for shadow mask and Fe-Ni-Co capable of providing excellent screen quality
A Cr-based alloy thin plate and a method for producing the same can be provided.

Further, according to the present invention as described above, even if annealing before press forming is performed before etching, required etching quality and press forming quality can be obtained. Fe-Ni for shadow masks that can omit
A Cr-based alloy thin plate and an Fe-Ni-Co-Cr-based alloy thin plate can be provided.

[Brief description of the drawings]

FIG. 1 is a graph showing the relationship between the occurrence of cracks during press forming, the degree of integration of {211} crystal planes, and the average austenite grain size after annealing before press.

FIG. 2 is a graph summarizing the relationship between the frequency of occurrence of transmission unevenness during press forming and the mixed grain size of austenite crystal grains after annealing before press forming.

FIG. 3 is a graph showing a relationship between austenite grain size after annealing before press and a cold rolling reduction in a single cold rolling.

FIG. 4 is a graph showing a relationship between a mixed grain size of austenite crystal grains after annealing before press and a first cold rolling reduction and a second cold rolling reduction in twice cold rolling.

FIG. 5 shows austenite grain size after annealing before press, mixed grain size of austenite grain size, {331}, {210},
4 is a graph summarizing the relationship between the degree of {211} crystal plane integration and annealing conditions before pressing.

────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. ⁶ Identification symbol FI H01J29 / 07 H01J29 / 07Z (56) References JP-A-6-57384 (JP, A) JP-A-6-57382 ( JP, A) JP-A-4-341543 (JP, A) (58) Fields investigated (Int. Cl. ⁶ , DB name) C22C 38/00-38/60 C21D 8/02, 9/46 H01J 9 / 14,29 / 07

Claims (5)

(57) [Claims] 1. In wt%, Ni: 34-38%, Cr:
0.05-3.0%, Si: 0.10% or less, B: 0.
0030% or less, O: 0.0030% or less, N: 0.0
030% or less, the average austenite crystal grain size D of the alloy sheet is 15 to 45 μm, the mixed grain size K of the austenite crystal grains determined by Equation 1 is 50% or less, and the degree of crystal plane integration on the surface of the alloy sheet Satisfies the values shown in Table 1, and has excellent press moldability.
e-Ni-Cr alloy thin plate. (Equation 1) Where K: mixed grain size of austenite crystals (%) D: average austenite grain size in alloy plate D _max : largest austenite grain size in alloy plate 2. In wt%, Ni: 34-38%, Cr:
0.05-3.0%, Co: 1.0% or less, Si: 0.
10% or less, B: 0.0030% or less, O: 0.003
0% or less, N: 0.0030% or less, the average austenite crystal grain size D of the alloy plate is 15 to 45 μm,
Particle size K of austenite crystal grains obtained by
A Fe—Ni—Cr—Co alloy thin plate for a shadow mask having excellent press moldability, wherein the degree of crystal plane integration on the surface of the alloy plate satisfies the values shown in Table 2. (Equation 2) Where K: mixed grain size of austenite crystals (%) D: average austenite grain size in alloy plate D _max : largest austenite grain size in alloy plate 3. In wt%, Ni: 27-38%, Cr:
0.05-3.0%, Co: more than 1.0% up to 7%, S
i: 0.10% or less, B: 0.0030% or less, O:
0.0030% or less, N: 0.0030% or less, and the average austenite grain size D of the alloy sheet is 15 to 4
5 μm, the mixed grain size K of austenite crystal grains determined by Equation 3 is 50% or less, and the degree of crystal plane integration on the surface of the alloy plate satisfies the values shown in Table 3. Fe-Ni-Cr-C for shadow mask
o Alloy sheet. (Equation 3) Where K: mixed grain size of austenite crystals (%) D: average austenite grain size in alloy plate D _max : maximum austenite grain size in alloy plate 4. A hot-rolled steel strip of an alloy having the composition according to claim 1, 2 or 3, after hot-rolled sheet annealing, and after first cold-rolling and subsequently recrystallization annealing, By performing finish cold rolling and performing strain relief annealing, when manufacturing an alloy thin plate for a shadow mask excellent in press formability, the hot rolled sheet annealing is performed at 810 to 890 ° C., and the first cold rolling is performed. The rolling reduction is 81 to 94%, and the rolling reduction in the finish cold rolling is 14 to 29%, respectively. Then, before the press forming, the annealing temperature is 740 to 900 ° C and the annealing time is 2 hours.
A method for producing an alloy sheet for a shadow mask having excellent press formability, wherein annealing is performed under conditions in which the annealing time T satisfies Expression 4 for up to 40 minutes. (Equation 4) Here, T: annealing temperature (° C.) t: annealing time (minute) 5. A hot-rolled steel strip of an alloy having the composition described in claim 1, 2 or 3 is subjected to hot-rolled sheet annealing, then subjected to primary cold rolling, and subsequently to primary recrystallization annealing. After secondary cold rolling and subsequent secondary recrystallization annealing, finish cold rolling and strain relief annealing to produce a shadow mask alloy sheet having excellent press formability. Hot rolled sheet annealing is performed at 810 to 890 ° C., and the rolling reduction in the first cold rolling is 40 to 55%, and the rolling reduction in the second cold rolling is 8
1 to 94%, and the rolling reduction in the finish cold rolling is in the range of 14 to 29%. Then, before the press forming, the annealing temperature is 740 to 900 ° C, the annealing time is 2 to 40 minutes, and the annealing temperature T A method for producing an alloy sheet for a shadow mask having excellent press formability, wherein annealing is performed under the condition that satisfies Equation 5. (Equation 5) Here, T: annealing temperature (° C.) t: annealing time (minute)