JPH0641686A - Stainless steel sheet for id blade and its production - Google Patents

Abstract

PURPOSE:To obtain a high strength steel for base material for an extra thin ID saw slicing machine excellent in breakage resistance and used, e.g. at the time of producing silicon wafer by specifying deformation stress and also specifying the composition of nonmetallic inclusions as inevitable impurities in the steel. CONSTITUTION:This sheet has a composition consisting of, by weight, 0.01-0.2% C, 0.1-2.0% Si, 0.1-2.0% Mn, 4.0-11.0% Ni, 13.0-20.0% Cr, 0.01-0.2% N, 0.0005-0.0025% sol. Al, 0.0020-0.0100% O, 0.0090% or less S, and the balance Fe and containing, if necessary, 0.08-0.90% Cu. Further, the amount of martensite at sheet thickness for ID blade is regulated to 40-90% and also deformation stress when a tensile deformation corresponding to 1.0% strain is applied is regulated to 1400N/mm<2> or less. Further, the nonmetallic inclusion as inevitable impurity in the steel has a composition in the region enclosed with the nonagon connecting the points 1 to 9 in the Al2O3-MnO-SiO2 ternary diagram in the figure.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an ultra-thin inner blade cutter (inner diameter) used in the production of silicon wafers.
The present invention relates to a high-strength stainless steel used as a substrate of a saw blade (ID blade) and a manufacturing method thereof.

[0002]

2. Description of the Related Art Conventionally, metastable austenitic stainless steel and precipitation hardening type (PH) stainless steel have been used as stainless spring materials used as ID blade substrates. However, recently, it has been a problem for users that the materials of these stainless steels are not stable and the probability of breakage is high.

By the way, the metastable austenitic stainless steel is represented by SUS301 and SUS304, and after the solution treatment, cold working is performed to generate work-induced martensite,
High strength can be obtained.
-44891 is disclosed. This technology uses C, N,
Using steel with the amounts of Si, Mn, Ni, Cr, and Mo adjusted so that Md ₃₀ is a predetermined value, CR ₃ is 40% or more, and the ratio of CR ₁ and CR ₂ (C
R ₁ / CR ₂ ) 0.8 or more, tensile strength 130kg / mm
By reducing the in-plane anisotropy of ² or more and strength,
We are trying to improve the flatness when tension is applied to the ID blade.

On the other hand, PH stainless steel is typified by SUS631, which has a single-phase martensite phase or a two-phase structure of austenite phase + martensite phase by cold working or sub-zero treatment after solution treatment, and is further aged. Perform precipitation hardening. Japanese Patent Application Laid-Open Nos. 61-295356 and 63-3176 disclosed as steels of this type.
28 is age-hardened by the combined addition of Si and Cu, and Hv = 5
80 is obtained, and further, a high crack generation stress (a value obtained by dividing the crack generation load by the plate thickness and the punch diameter) is attempted to improve the overhang workability.

[0005]

When the above-mentioned stainless steel is applied as an ID plate, the high probability of breakage during use poses a problem, which is a factor that significantly impedes productivity during wafer slicing. Has become. However, since there is no example in which the controlling factors of the breakage characteristics of the ID blade have been examined in the conventional techniques up to now, the breakage resistance cannot be improved.

That is, in the case of Japanese Examined Patent Publication No. 2-44891, the in-plane anisotropy is focused on, but the fracture characteristics are not considered at all. Further, in JP-A-61-29536 and JP-A-63-317628, the characteristics up to the time of tensioning are improved, but the breakage that occurs when used as a slicer after tensioning is not taken into consideration. In fact
JP-A-61-295356 and JP-A-63-317628
Since the PH stainless steel has extremely high strength and the size and amount of non-metallic inclusions contained therein are large, there is a problem that the probability of fracture during slicing is high even in a lot having good pullability.

[0007]

SUMMARY OF THE INVENTION The present invention has been devised through repeated studies in view of the problems of the prior art as described above, and the inventors of the present invention have developed a stainless steel thin plate excellent in fracture resistance. After carefully studying the manufacturing method, the following 3
The points turned out to be important. If the blade is made of stainless steel and stretched, the 1.0% onset stress in tensile deformation should be above a certain level and ductility should be ensured. In order to further reduce the fracture probability, the melting point of non-metallic inclusions should be lowered, the malleability should be increased and the thickness of inclusions should be reduced.
In addition, the amount of such non-metallic inclusions is reduced. Further, as one of the conditions for obtaining the above-mentioned stainless steel, the metastable austenitic stainless steel has a high martensite amount in an appropriate range, and is made fine by refining the crystal grains and reducing the effective martensite grain size as much as possible. A 1.0% onset stress can be obtained.

The present invention has been made on the basis of the above findings, and its features are as follows.

(1) In the plate thickness used as an ID blade, the deformation stress (hereinafter abbreviated as 1.0% onset stress) when a tensile deformation corresponding to 1.0% strain is applied is 1
The composition of the non-metallic inclusions, which is 400 N / mm ² or more and remains as unavoidable impurities in the steel, is Al ₂ O ₃ -MnO-of FIG.
A stainless steel thin plate for an ID blade, which has a composition of a region surrounded by a hexagon connecting points 1 to 9 in a SiO ₂ ternary phase diagram.

(2) C: 0.01 to 0.2% by weight,
Si: 0.1-2.0%, Mn: 0.1-2.0%, Ni: 4.0-
11.0%, Cr: 13.0 to 20.0%, N: 0.01 to 0.2
%, Sol.Al: 0.0005 to 0.0025%, O: 0.00
20-0.0100%, S: 0.0090% or less, and the balance Fe and unavoidable impurities. The amount of martensite in the plate thickness used as an ID blade is 4
A stainless steel thin plate for an ID blade, which has a content of inclusions of 1) and a condition of 1.0% onset stress, which is 0 to 90%.

(3) C: 0.01 to 0.2% by weight,
Si: 0.1-2.0%, Mn: 0.1-2.0%, Ni: 4.0-
11.0%, Cu: 0.08 to 0.90%, Cr: 13.0 to 20.
0%, N: 0.01 to 0.2%, sol.Al: 0.0005 to
0.0025%, O: 0.0020 to 0.0100%, S: 0.0.
The content of martensite in the plate thickness used as an ID blade is 40 to 90%, and the inclusion composition of item (1) and 1.0% onset are included. A stainless steel thin plate for an ID blade, which satisfies the stress condition.

(4) A first cold-rolled (CR ₁ ) − stainless steel strip having the components of the above (2) or (3) is applied after AP.
Intermediate annealing - second cold rolling (CR ₂₎ - intermediate annealing - third cold rolling (CR ₃₎ - final annealing - 4 cold rolling (CR ₄₎ - to produce the ID blade material at the aging treatment step On the occasion of 3
0% ≤ CR ₁ , CR ₂ , CR ₃ ≤ 60%, annealing temperature 9
50-1100 ° C, 66% ≤ CR ₄ ≤ 76%, then 3
A method for producing a stainless steel thin plate for an ID blade, which comprises performing low-temperature annealing at 00 to 600 ° C for 0.1 to 300 seconds.

[0013]

The function of the steel of the present invention will be described. The material for the ID blade needs to be stainless steel in order to secure the corrosion resistance when cutting the single crystal. Now, as a result of an examination on the controlling factors of the rupture resistance of the ID blade, the deformation stress (hereinafter referred to as 1.0% onset stress) when non-metallic inclusions and tensile deformation equivalent to 1.0% strain in the tensile curve are added. Has been found to be important. This 1.0 in Figure 1
Although the relationship of the% onset stress is shown, the steel of the present invention has a higher 1.0% onset stress than the comparative steel.

It is not clear why 1.0% onset stress affects rupture resistance, but since the ID plate is pulled up with a strain of about 1.0% with a tensioning bolt when used, 1.0% The deformation stress per strain of is considered to be an important factor. This 1.0% onset stress is 1
If it is 400 N / mm ² or more, the fracture characteristics are improved,
1.0% of stainless steel thin plate for ID blade according to the present invention
The onset stress was 1400 N / mm ² or more.

Further, in order to further enhance the fracture resistance when the ID blade is stretched and used, it is necessary to reduce the thickness of the inclusions that are likely to be the starting point of the fracture or reduce the amount thereof. Since the ID plate is an extremely thin material with a plate thickness of 0.3 mm or less, the influence of inclusions becomes remarkable. Regarding the control of the inclusions, it is effective to increase the malleability of the inclusions by lowering the melting point of the inclusions. Specifically, the composition of non-metallic inclusions remaining as unavoidable impurities in the stainless steel connects points 1 to 9 in the Al ₂ O ₃ —MnO—SiO ₂ system ternary phase diagram of FIG. It is necessary that the composition of the region surrounded by the hexagon is obtained.

Metastable austenitic stainless steel is one of the steels from which the above-mentioned stainless steel thin plate for ID blade can be obtained. The ingredients will be described below. C is an austenite forming element, and is required to be 0.01% or more in order to suppress δ-ferrite and strengthen work-induced martensite. However, if it exceeds 0.2%, a large amount of Cr carbide precipitates and the corrosion resistance and elongation deteriorate.
It was set to 0.2% or less.

Si is required to be 0.1% or more for solid solution strengthening austenite and work-induced martensite, but if added in excess, δ-ferrite precipitates and hot workability deteriorates, so 2.0. % Is the upper limit.

Mn is an austenite-forming element, and is required to be 0.1% or more for forming an austenite single phase by solution treatment and for deoxidation. However, if it exceeds 2.0%, the generation of the amount of processing-induced martensite is extremely suppressed.

Ni is an austenite forming element, 4.
If it is less than 0%, the austenite single phase does not form after annealing and 1
If it exceeds 1.0%, the austenite is excessively stabilized and sufficient work-induced martensite is not formed.
It was set to 11.0%.

From the viewpoint of its corrosion resistance, Cr is required to be 13.0% or more from the viewpoint of corrosion resistance. If it exceeds 20.0%, the amount of ferrite increases and the hot workability deteriorates.
It was set to ~ 20.0%.

Cu is an element that is preferably added in order to strengthen the structure of the passivation film and further improve the corrosion resistance as an ID blade material. The corrosion resistance can be improved by adding 0.08% or more, but the effect is saturated and the hot workability is deteriorated even if it is added in excess of 0.90%.
Therefore, the more preferable Cu amount for improving the corrosion resistance is 0.08-
It is 0.90%.

N is an austenite forming element and a solid solution hardening element of martensite, so 0.01% or more is necessary, but 0.2% is added because a large amount of addition causes blow holes during casting. Below.

S forms MnS, and the inclusions are likely to be the starting point of fracture, resulting in a high fracture probability. S
If the amount exceeds 0.009%, the fracture probability increases, so 0.0
The upper limit was 09%. 1.0% due to such reduction of S
It is possible to reduce the fracture probability of a material having a high onset stress.

Sol.Al determines the number and composition of non-metallic inclusions. If it exceeds 0.0025%, the oxygen content in the molten steel is less than 0.0020% and the number of inclusions decreases. Since it becomes an Al ₂ O ₃ system, surface defects occur, and this defect easily becomes a starting point of fracture, resulting in a high probability of fracture. If the sol.Al content is less than 0.0005%, the oxygen content in the molten steel exceeds 0.0100%, the number of inclusions increases, and the composition of the inclusions increases the melting point of the MnO-SiO2 _binary system.
It becomes Cr ₂ O _{3 and the} drawability during hot is deteriorated, and such inclusions also tend to be the starting point of fracture, resulting in a high fracture probability. Therefore, as shown in FIG. 3, an Al ₂ O ₃ —MnO—SiO ₂ type inclusion having a low melting point and hot drawability is used, and by making the thickness of the inclusion as thin as possible, the inclusion is unlikely to be a starting point of fracture. So sol.Al is 0.0005 ~
0.0025% and O were 0.0020 to 0.0100%.
In order to obtain such an inclusion composition, a ladle made of MgO-CaO refractory with CaO of 50% or less is used in ladle refining after tapping, and the slag component is wt%. [CaO]
/ [SiO _{2]: 1.0~4.0, Al 2 O 3:} 3% or less, MgO: 1
5%, CaO: it is desirable to use a 30 to 80 percent of CaO-SiO ₂ -Al ₂ O ₃ system.

In the steel of the present invention, the balance other than the above-mentioned constituent elements is basically Fe, but Ca, REM, and other unavoidable impurities for the purpose of controlling the morphology of sulfides and improving hot workability. Can be included.

On the other hand, the present inventors have examined in detail the material factors for increasing the 1.0% onset stress. As a result 1.
It has been found that the amount of martensite needs to be proper and that the effective grain size of martensite and the aging condition described later need to be optimized in order to increase the 0% onset stress. That is, Fig. 2 shows the effects of 1.0% onset stress and martensite amount on the fracture characteristics. In order to set the 1.0% onset stress to 1400 N / mm ² or more, the martensite effective described later is used. After adjusting the particle size and aging conditions appropriately,
It is necessary to set the amount of martensite to 40% or more. However, if the amount of martensite exceeds 90%, the ductility decreases, leading to fracture during stretching. Therefore, 40-90% of the amount of martensite is suitable.
It should be noted that even if the amount of martensite in FIG. 2 is in the range of 40 to 90%, the one having a 1.0% stress of less than 1400 N / mm ² is a comparative example (material No. 20, 23, 27) in Examples described later. It is a thing.

A method for manufacturing the above-mentioned 1.0% onset stress-increasing stainless steel thin plate for ID blades having excellent rupture resistance was established as follows. That is, the first cold rolled (CR ₁ )-
Intermediate annealing - second cold rolling (CR ₂₎ - intermediate annealing - third cold rolling (CR ₃₎ - final annealing - 4 cold rolling (CR ₄₎ - in the step of aging _{treatment, 30% ≦ CR 1, CR} 2 , CR ₃ ≤ 6
0%, annealing temperature 950 to 1100 ° C, 66% ≤ CR ₄
≤76%, then 300-600 ℃ x 0.1-300sec
Low temperature annealing, 1.0% onset stress ≧ 1400N
/ Mm ² , martensite amount: 40 to 90%.

Explaining the reasons for limiting the manufacturing method as described above, the stainless steel strip having the above-described composition is subjected to AP first cold rolling (CR ₁ ) -intermediate annealing-second.
In a series of steps of cold rolling (CR ₂ ) -intermediate annealing-third cold rolling (CR ₃ ) -final annealing, cold rolling-annealing is repeated.
An extremely fine recrystallized structure is obtained by annealing at 0 to 1100 ° C, and at the same time, fine carbides are precipitated with each annealing to reduce the effective grain size of martensite after finish rolling (desirably 200 Å or less). I am trying to It is preferable that the number of times of this repetition is large, but if it is too large, it will be complicated in the production, so it was made 3 times.

Next, as described above, in the first to third cold rolling conditions, when the rolling reduction is less than 30%, the structure after annealing tends to be a mixed grain structure and the material tends to become nonuniform, and even if it exceeds 60%. Since further miniaturization cannot be expected and the rolling load increases, 3
It was set to 0 to 60%. By these treatments, the ductility can be secured while the strength is high, and the fracture resistance can be improved.

FIG. 4 shows the effective martensite grain size, 1.0.
The effect of annealing temperature on% onset stress and corrosion resistance is shown. When the annealing temperature is lower than 950 ° C, the effective grain size of martensite is fine and the 1.0% onset stress is 1400 N /
mm ² or more can be secured, but rust occurs due to the large amount of precipitated carbide. When the annealing temperature exceeds 1100 ° C,
Although carbides form a solid solution and exhibit good corrosion resistance, the effective grain size of martensite increases and the 1.0% onset stress decreases. By annealing at 950 to 1100 ° C., the martensite effective grain size becomes finer and a high 1.0% onset stress can be obtained, and in this range, precipitation of carbides is extremely fine and rusting does not occur.

Next, finish cold rolling (CR ₄ ) is 66 to 76%.
The reason is that the content of martensite is 40 to 90%.
This is to increase the 1.0% onset stress. However, 66
If it is less than 40%, the martensite content is less than 40%, while if it exceeds 76%, the martensite content exceeds 90% and the ductility becomes poor. 30 more
The strength and 1.0% onset stress are further improved by performing low temperature annealing at 0 to 600 ° C for 0.1 to 300 seconds.
This further improves the fracture resistance. If the low temperature annealing temperature is less than 300 ° C, the aging is incomplete and the temperature is 1400 N / mm.
^If the 1.0% onset stress of ² or more cannot be obtained, and the reverse transformation austenite is generated and the 1.0% onset stress is lowered when the temperature exceeds 600 ° C., the low temperature annealing temperature is 300 to 600.
℃ was made. Also, if the soaking time is less than 0.1 sec, the aging is incomplete, so the 1.0% onset stress is less than 1400 N / mm ² , and even if it exceeds 300 sec, there is no further improvement in the properties, rather at around 600 ° C. In the temperature range of 1, the reverse transformation austenite is generated and the 1.0% onset stress is lowered, so it was set to 0.1 to 300 seconds. A desirable low temperature annealing condition for increasing the 1.0% onset stress is 400 to 500 ° C. × 2 to 8 seconds.

By manufacturing according to the various conditions as described above, it is possible to accurately manufacture a stainless steel thin plate for an ID blade, which is made of a stable material and has a very low probability of breakage. The stainless steel for ID blades according to the present invention is not limited to the above metastable austenitic stainless steel, but may be martensitic PH stainless steel, austenitic PH stainless steel, or semi-austenitic PH stainless steel. In addition, the stainless steel for ID blades according to the present invention is obtained by casting a thin cast plate after melting,
A thin steel strip after casting or hot working may be used as the material.

[0033]

EXAMPLES To describe specific examples according to the present invention as described above, the present inventors first produced 20 kinds of steel having the chemical components shown in Table 1 below. A ~ J
Is an invention steel, and K to T are comparative steels.

[0034]

[Table 1]

The production conditions after hot rolling for each of the above steels were changed as shown in Tables 2 and 3 below, and the material N
o. Each material of 1-27 was obtained. That is, Nos. 1 to 16 are steels that satisfy the requirements of the present invention, and Nos. 17 to 2 are used.
7 is a comparative steel. Here, No. 17, 1
Except for 8, 25 and 26, CaO in ladle refining after tapping:
Using the ladle consisting of 50% or less of MgO -CaO based refractory components of溶滓are in wt% [CaO] / [SiO _2]: 1.0 to 4.
0, Al ₂ O ₃ : 3% or less, MgO: 15% or less, CaO: 30
It was obtained by using those 80% of CaO-SiO ₂ -Al ₂ O ₃ system.

[0036]

[Table 2]

[0037]

[Table 3]

Table 4 below shows the mechanical properties of the products obtained as described above. That is, in Table 4, the effective grain size of martensite was obtained from the following two equations by X-ray diffraction and Hall.

[0039]

[Formula 1]

The measurement was carried out on martensite (211),
The diffraction peak width of the (422) diffraction surface was used. Further, the thickness of inclusions was measured in the plate thickness direction, and the number per 10 mm ² was determined by size. In addition, the breaking probability was obtained, and a small punch test was performed to measure the work amount up to the breaking to evaluate the pulling property.

[0041]

[Table 4]

According to the results shown in Table 4 above, each of the Nos. 1 to 15 of the invention steels has a higher 1.0% onset stress and a higher work amount in the small punch test than the comparative steels, and does not fracture. Corrosion resistance is also good. No. 16 had good mechanical properties, but had a small amount of Cu and therefore had slightly poor corrosion resistance. No. 17,
In No. 18, a small punch test and a fracture characteristic test were found to have fractures originating from inclusions. In addition, it is specified in the present invention
As shown in Table 1, the inclusions of the invention alloys in the ranges of sol.Al and O content are Al ₂ O ₃ -MnO-SiO ₂ -based inclusions having a melting point of 1400 ° C. or less, which are elongated in the rolling direction, and A, It was a thin inclusion having a thickness of less than 3 μm in the B type and less than 5 μm in the C type.

In contrast to the steel according to the present invention as described above, the sol. Al and O contents outside the range specified by the present invention are No. 1
The spherical inclusions No. 7 and No. 18 had a high Al ₂ O ₃ content. No. 19 has a high S content and a large amount of sulfide-based inclusions, and therefore has a high probability of fracture and poor corrosion resistance. No. 20 is a 3 cold-rolled material according to the prior art (Japanese Patent Publication No. 2-44891), but the crush resistance of the steel of the present invention is inadequate due to insufficient crystal grain refinement and effective martensite grain size reduction. Inferior. N
Since o.21 has a low martensite content, the 1.0% onset stress is low and the fracture probability is high. No. 22
Has a high finishing reduction rate and an excessive amount of martensite, resulting in poor ductility. Therefore, the amount of work during stretching is small and the fracture probability is extremely high. No. 23 has incomplete aging due to low low temperature annealing temperature and 1.0% onset stress is 1400 N / mm.
Since it is less than ^2, it may break. No. 24 and 27
Since the low temperature annealing temperature is high, the reverse transformation austenite is generated and the 1.0% onset stress is significantly reduced, so that the fracture probability is high. No. 25 and No. 26 were found to have fractures starting from inclusions in the fracture characteristic test.

[0044]

According to the present invention as described above, it is possible to obtain a stable high-strength stainless steel thin plate having a low probability of breakage, and to provide a steel plate suitable for a stainless steel spring as well as a substrate for an ID blade. It is an invention that is industrially highly effective.

[Brief description of drawings]

FIG. 1 is a chart showing how to determine 1.0% onset stress and its relationship.

FIG. 2 is a chart showing the effects of 1.0% onset stress and martensite content on fracture properties.

FIG. 3 is an Al ₂ O ₃ —MnO—SiO ₂ system ternary phase diagram, in which the liquidus temperature of inclusions and the range of the present invention, point 1 (Al ₂ O ₃ : 21)
%, MnO: 12%, SiO ₂ : 67%), point 2 (Al ₂ O ₃ : 19)
%, MnO: 21%, SiO ₂ : 60%, point 3 (Al ₂ O ₃ : 15)
%, MnO: 30%, SiO ₂ : 55%), point 4 (Al ₂ O ₃ : 5%,
MnO: 46%, SiO ₂ : 49%), point 5 (Al ₂ O ₃ : 5%, MnO:
68%, SiO ₂ : 27%, point 6 (Al ₂ O ₃ : 20%, MnO: 6)
1%, SiO ₂ : 19%), point 7 (Al ₂ O ₃ : 27.5%, MnO: 5)
0%, SiO ₂ : 22.5%), point 8 (Al ₂ O ₃ : 30%, MnO: 3)
8%, SiO ₂ : 32%, point 9 (Al ₂ O ₃ : 33%, MnO: 27)
%, SiO ₂ : 40%) is a diagram showing a region inside a rounded polygon.

FIG. 4 Martensite effective grain size at the final annealing temperature and
It is a chart showing the influence on the rusting area of 1.0% onset stress and salt spray test.

─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. ⁵ Identification code Internal reference number FI technical display location H01L 21/78 F 8617-4M // H01L 21/304 321 S 8728-4M (72) Inventor Large Tomoyoshi Kita, 1-2-1, Marunouchi, Chiyoda-ku, Tokyo Nihon Steel Tube Co., Ltd.

Claims (4)

[Claims] 1. A plate having a plate thickness used as an ID blade has a deformation stress (hereinafter referred to as 1.0% onset stress) of 140 when tensile deformation equivalent to 1.0% strain is applied.
0N / mm ² or more, Al ₂ O ₃ -MnO -SiO ₂ composition of nonmetallic inclusions remain as unavoidable impurities in the steel 3
A stainless steel thin plate for an ID blade, which has a composition of a region surrounded by a hexagon connecting points 1 to 9 in a system ternary diagram. 2. C: 0.01 to 0.2% by weight, S
i: 0.1-2.0%, Mn: 0.1-2.0%, Ni: 4.0-1
1.0%, Cr: 13.0 to 20.0%, N: 0.01 to 0.2
%, Sol.Al: 0.0005 to 0.0025%, O: 0.00
20-0.0100%, S: 0.0090% or less, and the balance Fe and unavoidable impurities. The amount of martensite in the plate thickness used as an ID blade is 4
A stainless steel thin plate for an ID blade, wherein the content is 0 to 90% and satisfies the inclusion composition and 1.0% onset stress conditions of claim 1. 3. By weight%, C: 0.01 to 0.2%, S
i: 0.1-2.0%, Mn: 0.1-2.0%, Ni: 4.0-1
1.0%, Cu: 0.08 to 0.90%, Cr: 13.0 to 20.0
%, N: 0.01 to 0.2%, sol.Al: 0.0005 to 0.
0025%, O: 0.0020 to 0.0100%, S: 0.0
The content of martensite in the plate thickness used as an ID blade is 40 to 90%, containing less than 090%, the balance being Fe and unavoidable impurities, and the inclusion composition and 1.0% onset stress of claim 1. A stainless steel thin plate for an ID blade, which satisfies the above condition. 4. A stainless steel strip having the composition according to claim 2 or 3 after AP first cold rolling (CR ₁ ) -intermediate annealing-second
In the process of cold rolling (CR ₂ ) -intermediate annealing-third cold rolling (CR ₃ ) -final annealing-fourth cold rolling (CR ₄ ) -aging treatment
When manufacturing blade materials, 30% ≤ CR ₁ , C
R ₂ , CR ₃ ≦ 60%, annealing temperature 950 to 1100
℃, 66% ≤ CR ₄ ≤ 76%, then 300-600 ℃
A method for manufacturing a stainless steel thin plate for an ID blade, which comprises performing low temperature annealing for 0.1 to 300 seconds.