JP2006233250A - Ferritic stainless steel sheet for formed spring and manufacturing method therefor - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide an inexpensive ferritic stainless steel sheet for a formed spring, which has spring characteristics comparable to those of austenitic stainless steel used for various formed springs, and uses few expensive component elements such as Ni, and to provide a manufacturing method therefor. <P>SOLUTION: The ferritic stainless steel for the sheet comprises not more than 0.03% C, not more than 0.03% N, not more than 1.00% Si, not more than 1.00% Mn, 16-20% Cr, not more than 0.60% Ni, 8×(C+N)% to 0.80% Nb by mass% and the balance Fe with unavoidable impurities. The method for manufacturing the sheet comprises the steps of: cold-rolling the ferritic stainless steel so as to store distortion corresponding to that stored by cold rolling with a reduction of 15% or higher inside it; and subjecting to final heat treatment in a temperature range of 550 to 750°C. Thus manufactured stainless steel sheet has a 0.2% yield strength σ of 600 MPa or higher, and such elongation ε(%) as to satisfy both relationships of ε≥-0.02×σ+22 and ε≥5. <P>COPYRIGHT: (C)2006,JPO&NCIPI

Description

  The present invention relates to a ferritic stainless steel sheet for molded springs, which is excellent in workability and used for various molded springs, and a method for producing the same.

  The austenitic stainless steel plate used for various shaped springs has a high work hardening coefficient. For example, SUS304 having a typical composition has a tensile elongation of about 30% even if it is rolled by 10% and exhibits a hardness of about Hv300. However, the additive element Ni itself is expensive and has low price stability. For this reason, utilization of the ferritic stainless steel sheet with the small Ni addition amount which can express the characteristic which can be substituted is desired.

  However, the ferritic stainless steel sheet has a low work hardening coefficient. For example, in the case of SUS430 having a typical composition, if it is attempted to obtain the same strength as that of an austenitic stainless steel, the tensile elongation is 2 at a rolling rate of 70%. % Or less, the desired ductility cannot be ensured. For this reason, ferritic stainless steel has been generally recognized as having low utility value in fields where high strength and workability are required, such as spring materials.

  Various proposals have been made so far to improve the properties of ferritic stainless steel. For example, Patent Document 1 proposes “a soft ferritic stainless steel with small anisotropy and excellent deep drawability”. On the second page of the same document, “C and N are fixed to impart softness to the steel and suppress coarsening and embrittlement of crystal grains, thereby improving the workability of the steel, particularly the deep drawability of the present invention. Although it is described as “effective element” and processability is obtained by reducing the amount of C and N by adding Nb, the problem is softening of the material, which is aimed at producing a material for deep drawing.

  Patent Document 2 proposes “a ferritic stainless steel plate excellent in workability and a manufacturing method thereof”. In paragraph 0010 of the same document, it is described as “providing a ferritic stainless steel sheet having excellent workability by using Nb-based precipitates for controlling crystal orientation”. The final annealing temperature is as high as 900 ° C. to 1100 ° C. (paragraph 0029), and is intended to be hard-worked after softening the steel plate.

  Thus, ferritic stainless steel has low recognition as a spring application due to a low work hardening coefficient. For example, Patent Literature 3 and Patent Literature 4 can be cited as proposals for using ferritic stainless steel as a spring.

  Patent Document 3 proposes a “manufacturing method of high strength and high toughness ferritic stainless steel”. In this document, Ti is used as an additive element, and the relationship between the control value determined by the addition amount of C, N and Ti, the solution treatment temperature, the cold rolling rate and the spring limit value is described. The annealing temperature range is 400 ° C. or less, and page 3 of the same document “The aging temperature exceeds 400 ° C. causes overaging, and solid solution C and N have a small effect of forming carbonitrides and fixing dislocations. It is not trying to obtain the ductility necessary for molded springs.

  Patent Document 4 proposes “a ferritic stainless steel plate for springs and a manufacturing method thereof”. Page 4 of the same document describes "the effect of suppressing the characteristic deterioration when the softening start temperature is moved to the high temperature side and the product spring is post-heat treated at 550 to 600 ° C", but the addition of Nb and Ti The amount is specified in a small range of 0.1% by mass or less, and the design is less than the amount of addition required for imparting corrosion resistance ((C + N) 8% by mass or more). As a “element indispensable for realizing high spring characteristics”, Si is positively used for strengthening by a solid solution element.

Thus, the invention which has a spring characteristic (corrosion resistance, intensity | strength, ductility) comparable with the conventionally used austenitic stainless steel has not yet been made.
Japanese Patent Publication No. 51-29694, page 2 JP2002-194508, paragraph 0010,0029 JP-A-5-287375 JP 2001-123248, page 4

  The present invention has been made in order to solve the above problems, and has spring characteristics comparable to austenitic stainless steels used for various molded spring materials, and is a high-priced component such as Ni. An object of the present invention is to provide a low-cost ferritic stainless steel sheet for molded springs that uses almost no elements and a method for producing the same.

  In the present invention, a sufficient amount of Nb that is consumed as carbonitride is added, C and N that are supersaturated by pre-strain are used, precipitation hardening is used in heat treatment in an overage region, and a special solid solution strengthening element is used. It was made possible to obtain high spring characteristics without the need for The specific means will be described below.

  The ferritic stainless steel sheet for molded springs of the present invention is in mass%, C: 0.03% or less, N: 0.03% or less, Si: 1.00% or less, Mn: 1.00% or less, Cr: Ferrite stainless steel containing 16 to 20%, Ni: 0.60% or less, Nb: 8 × (C + N)% or more and 0.80% or less, the balance being Fe and inevitable impurities, 15% By accumulating the processing strain corresponding to the cold rolling described above, and finally heat-treating in a temperature range of 550 ° C. or more and 750 ° C. or less, it has a 0.2% proof stress σ of 600 MPa or more and It is characterized by exhibiting an elongation ε (%) that satisfies both equations.

ε ≧ −0.02 × σ + 22 (1)
ε ≧ 5 (2)
The manufacturing method of the ferritic stainless steel sheet for molded springs of the present invention is, in mass%, C: 0.03% or less, N: 0.03% or less, Si: 1.00% or less, Mn: 1.00% or less. , Cr: 16 to 20%, Ni: 0.60% or less, Nb: 8 × (C + N)% or more and 0.80% or less, respectively, with respect to a ferritic stainless steel whose balance is Fe and inevitable impurities , After accumulating processing strain corresponding to 15% or more of cold rolling inside, final heat treatment is performed in a temperature range of 550 to 750 ° C., 0.2% proof stress σ is 600 MPa or more, and elongation ε (% ) Is a steel plate satisfying both the relations of (1) Formula ε ≧ −0.02 × σ + 22 and (2) Formula ε ≧ 5.

  When a rolled steel material is annealed in an overaged region where ductility is restored, the strength tends to decrease in a normal case. However, in the present invention, a desired pre-strain (corresponding to a cold rolling of 15% or more) is achieved by cold rolling. By subjecting the ferritic stainless steel to which the processing strain is given) to a final heat treatment in an overaging region (550 to 750 ° C.), the precipitation aging of Nb carbide and Nb carbonitride is actively caused, thereby Compensates for a drop in strength. As a result, 0.2% yield strength σ of 600 MPa or more is obtained as desired spring characteristics. Such a 0.2% yield strength σ is given to the steel material existing in the right region R2 from the critical characteristic line CL1 shown in FIG.

  On the other hand, in the present invention, component design of main component elements C, N, Nb, Cr, Si, and Mn is performed with respect to ductility among various characteristics, and the desired elongation ε is minimized by minimizing the decrease in ductility associated with precipitation aging. This makes it possible to mold the spring. As a result, an elongation ε satisfying both the above equations (1) and (2) is obtained as a desired spring characteristic. Such an elongation ε is given to the steel material existing in the region R2 above the critical characteristic lines CL2 and CL3 shown in FIG.

  In the present invention, one or two of Cu: 0.80% or less and Mo: 2.50% or less can be further contained by mass%. When Cu and Mo are added within a range that does not impair the workability, the strength and corrosion resistance are further improved.

  Below, the effect | action of each component element in this invention, rolling conditions, and the reason for limitation of heat processing conditions are each demonstrated.

1) C: 0.03 mass% or less
In general, as the C content increases, the corrosion resistance, oxidation resistance, workability, and toughness decrease. In the present invention, precipitation hardening is caused by making solid solution C supersaturated by utilizing pre-strain by cold rolling and reacting Nb which is a stabilizing element with C in the overaging region. In order to stably precipitate Nb carbide and Nb carbonitride in the overaging region and cause aging precipitation hardening, if the C content is unnecessarily increased, the Nb addition amount must be increased. The upper limit of the amount was set to 0.03% by mass of the low carbon level that can be controlled by normal operation.

2) N: 0.03 mass% or less
N is an interstitial element similar to C, and N that is supersaturated by rolling pre-strain forms Nb and carbonitride and contributes to precipitation hardening. Therefore, in order to obtain the desired effect of the present invention, if the N content is increased unnecessarily, the Nb addition amount must be increased, so that the upper limit of the N content can be controlled by normal operation. It was set to 0.03% by mass of the level.

3) Si: 1.00 mass% or less
Si is an element that contributes to the improvement of the material strength and is effective in improving the high-temperature oxidation characteristics. However, workability and toughness deteriorate when Si is added in excess of 1.00% by mass. Therefore, the upper limit of Si content was set to 1.00% by mass.
Incidentally, in the steel of Patent Document 4, Si is positively added as an indispensable element for realizing high spring characteristics in order to obtain a Vickers hardness Hv310 or more as a characteristic required for the spring.

4) Mn: 1.00% by mass or less
Mn is an element that is particularly effective for improving the scale peelability among the high-temperature oxidation characteristics, but since it does not contribute to the precipitation hardening of the present invention even if the amount of Mn is increased, it is usually contained in ferritic stainless steel. The upper limit was about 1.00% by mass.

5) Cr: 16 to 20% by mass
Cr is an element that stabilizes the ferrite phase and improves the corrosion resistance and heat resistance. In order to obtain the desired corrosion resistance, it is necessary to add at least 16% by mass of Cr. However, if Cr is contained in a large amount, not only the raw material cost is increased, but if it is added in excess of 20% by mass, the workability is rather disturbed, so 20% by mass was made the upper limit.

6) Ni: 0.6 mass% or less
Ni is an element that contributes to improvement in material strength and corrosion resistance, but it is expensive and has low price stability. In the present invention, since the effect of addition of Ni is not expected, the upper limit is set to 0.6% by mass as stipulated in Japanese Industrial Standard (JIS) as the amount of Ni allowed to be normally contained in ferritic stainless steel.

7) Nb: 8 × (C + N) mass% or more and 0.8 mass% or less
Nb fixes carbon and nitrogen as forming elements such as carbonitrides, and prevents deterioration of corrosion resistance due to the generation of Cr-deficient layers, thereby suppressing grain boundary migration by the generated carbonitrides and aiming to improve heat resistance To be added. Nb needs to be added at least 8 times as much as (C + N) mass% by the amount of C and N in order to fix C and N and prevent deterioration of corrosion resistance due to generation of a Cr-deficient layer. Since it is necessary to contain more Nb in order to aim at the effect (softening temperature rise, precipitation hardening) of molten Nb, the lower limit is more than 8 × (C + N) mass%, and the upper limit is an economic reason. And from the suppression of ductility reduction, it was made 0.80%.

  In the steel of the present invention, a sufficient amount of Nb more than that consumed as carbonitride is added, and C and N which are supersaturated by pre-strain are used, and high spring characteristics are obtained by precipitation hardening by heat treatment in the overaging region. Trying to get. Nb fixing C and N as precipitates exists in the form of Nb (C, N) from hot rolling to final annealing, and the amount and precipitation state hardly change.

  Incidentally, the second page of Patent Document 1 states that “Nb fixes C and N, imparts softness to the steel, suppresses crystal grain coarsening and embrittlement, and makes the steel workability particularly the deep drawability of the present invention. It is an element that is effective in improving the quality of the material "and has obtained workability by reducing the amount of C and N by adding Nb, but the problem is softening the material, and the purpose is to produce the material for deep drawing applications It is said.

  Incidentally, on page 4 of Patent Document 4, it is described as “the effect of suppressing the deterioration of characteristics when the softening start temperature is moved to the high temperature side and the product spring is post-heat treated at 550 to 600 ° C.” The Nb addition amount is regulated to a small range of 0.1% by mass or less. Furthermore, according to the component range shown on the 4th page of Patent Document 4, (C + N) mass% is 0.04 to 0.24%, and Nb required for imparting corrosion resistance is used. The addition amount is 0.32 to 3.84% if it is required 8-16 times or more of (C + N) mass%, but the Nb addition range is designed to be lower than that.

8) Cu: 0.80 mass% or less
Cu is an element effective for improving corrosion resistance and strength, and also effective for imparting antibacterial properties, so it is added depending on the use environment. However, when Cu is added excessively exceeding 0.80 mass%, the hot workability is lowered and the workability is deteriorated, so 0.80 mass% was made the upper limit.

9) Mo: 2.50 mass% or less
Mo is an element effective for improving corrosion resistance and strength, and is added depending on the use environment. However, when Mo is added in excess of 2.50% by mass, the hot workability is lowered and the workability is deteriorated, so 2.50% by mass was made the upper limit.

10) Other additives and inevitable impurities
In the ferritic stainless steel targeted by the present invention, other alloy elements other than those described above are not particularly specified, and are appropriately added as necessary. As an additive component of this type, Ca, Mg, and B can be added at a trace level of 0.05% by mass or less as elements effective for improving hot workability and toughness.

  P, S, and O are desirably kept as low as possible to a level close to the detection limit of a general-purpose component analyzer in order to deteriorate strength and workability. However, when it is inevitably mixed as an impurity in the steelmaking process, P is controlled to 0.04% by mass or less, S is controlled to 0.03% by mass or less, and O is controlled to 0.02% by mass or less to deteriorate workability. To prevent.

11) Rolling rate: Work strain equivalent to 15% or more cold rolling
When aiming at an improvement effect of spring characteristics by precipitation hardening of Nb carbide and Nb carbonitride, it is necessary to accumulate a working strain corresponding to cold rolling of at least 15% or more in the steel sheet. If the processing strain is less than 15%, the amount of precipitation of Nb carbide and Nb carbonitride becomes insufficient, and the spring properties (tensile strength, 0.2% proof stress, elongation, hardness) do not improve to the desired level. .

  Here, “working strain corresponding to cold rolling of 15% or more” refers to processing strain that adds lattice strain in which the solid solution C is supersaturated C that can be combined with Nb in a temperature region lower than the recrystallization temperature. Say. This is because the lattice strain cannot be applied at a rolling rate of less than 15% in cold rolling. When used as a molded spring material, a molding process such as bending is often added, and stress is concentrated in the shape of the processed part, and the spring characteristics are compensated at that part. Even steel sheets produced with a rolling rate of less than 15% can be further distorted by bending, and equivalent characteristics can be obtained by heat treatment in the overaging region. Therefore, in the present invention, the expression “corresponds to...” Is used. Note that the upper limit of the rolling rate is not specified in the present invention because of the processing limit for each component and the increase in manufacturing cost.

12) Final heat treatment temperature: 550 ° C or higher and 750 ° C or lower
In order to retain the workability required as a molded spring material using the overaging temperature range, final annealing is performed in a temperature range of 550 to 750 ° C. (more preferably 600 to 700 ° C.). The temperature range of 550 to 750 ° C. is a temperature range that is higher than the strain aging temperature and lower than the recrystallization temperature at which processing strain can be completely removed.

  Incidentally, paragraph 0010 of Patent Document 2 describes that "by using Nb-based precipitates for controlling crystal orientation ... (Omitted) to provide a ferritic stainless steel sheet having excellent workability". However, the final annealing temperature is as high as 900 ° C. to 1100 ° C. (paragraph 0029), and is intended to be hard-worked after softening the steel plate.

  Incidentally, in Patent Document 3, the final annealing temperature range used for the aging heat treatment is 400 ° C. or less, and it is described on page 3 of the same document as “Aging temperature exceeds 400 ° C., causing overaging, and solute C and N are carbon. This is different from the steel of the present invention in that the effect of forming nitrides and fixing dislocations is reduced.

  According to the steel of the present invention, the Nb-containing ferritic stainless steel subjected to a specific pre-strain has sufficient strength and workability as a molded spring material by performing a final heat treatment at a specific over-aging temperature. Ferritic stainless steel is provided. Moreover, according to this invention, the manufacturing method of the ferritic stainless steel which can be stably produced is provided.

  The best mode for carrying out the present invention will be described below with reference to the accompanying drawings.

Various ferritic stainless steels having the compositions shown in Table 1 were melted in a vacuum melting furnace, cut into slabs having a thickness of about 50 mm, heated to 1200 ° C., and hot rolled to a plate thickness of 3 mm. Further, soft annealing at 750 to 920 ° C. and cold rolling were repeated to produce a cold rolled annealing material having a thickness of 1 mm.

Example 1
Using a steel sheet having the chemical composition shown in Example 1 of Table 1, cold rolling at a rolling rate of 30 to 70% was performed, and heat treatment was performed at each temperature. 2% yield strength σ and elongation ε were evaluated (FIGS. 1 and 2).

  FIG. 1 is a characteristic diagram showing the results of investigating the correlation between the various samples with the heating temperature (° C.) of the final heat treatment on the horizontal axis and the Vickers hardness Hv (load 1 kg) of various samples on the vertical axis. In the figure, the characteristic line A1 (white circle) indicates the rolling rate of 30%, the characteristic line A2 (white triangle) indicates the rolling rate of 50%, and the characteristic line A3 (white square) indicates the rolling rate of 70%. As is apparent from the figure, the material hardness varies depending on the rolling rate, and the effect of the aging heat treatment becomes more remarkable when the rolling rate is 50% or more, exceeding the hardness after rolling by precipitation of carbonitride in a temperature region around 600 ° C. The hardness of Hv320 was obtained at the maximum. Although the softening start temperature slightly changed depending on the rolling rate, the hardness as-rolled was maintained up to 750 ° C.

  In FIG. 2, the horizontal axis indicates the heating temperature (° C.) of the final heat treatment, and the vertical axis indicates the tensile strength (MPa), 0.2% proof stress σ (MPa), elongation ε (%), and Vickers hardness Hv of various samples. It is a characteristic diagram which shows the result of having investigated (each load 1kg) about each correlation. The rolling rate was 70%. In the figure, the characteristic line B indicates the tensile strength, the characteristic line C indicates the 0.2% yield strength σ, the characteristic line D indicates the Vickers hardness Hv, and the characteristic line E indicates the elongation ε. As is clear from the figure, it was confirmed that the ductility recovered with the heating temperature at 70% rolled material, exceeded 6% at 550 ° C., and the temperature range where both the ductility and hardness were stable was 550 to 700 ° C., A material having a material hardness Hv of 290 to 320 and an elongation of 6 to 8% was obtained. At a temperature lower than 550 ° C., there is no decrease in the material hardness, but the ductility is not sufficiently recovered. At a temperature higher than 750 ° C., the ductility is recovered.

  Also in the steel types of Examples 2 and 3, when the same confirmation as in Example 1 was performed, the heating conditions of the final heat treatment for obtaining stable quality were in the temperature range of 550 to 750 ° C., and the mechanical characteristic values at that time (0.2% proof stress, elongation) is shown by a black circle plot in FIG. On the other hand, even if the composition is in the range of the present invention, a white circle in FIG. 5 is used as a comparative example in which the manufacturing conditions (final heat treatment temperature 400 to 550 ° C.) are out of the range of the present invention. Shown in the plot. Further, the mechanical properties as rolled are shown as white square plots in FIG. 5 as a conventional example.

  FIG. 5 shows the results of examining the 0.2% yield strength σ and the elongation ε of various steel sheets, with the horizontal axis representing 0.2% yield strength σ (MPa) and the vertical axis representing elongation ε (%). FIG. Black circles in the figure are examples (composition is within the range of the present invention, final heat treatment temperature is 550 to 750 ° C.), white circles are comparative examples (composition is within the range of the present invention, final heat treatment temperature is 400 to 550 ° C.), white squares are The results of conventional examples (composition within the scope of the present invention, as-rolled) are shown. Three lines CL1, CL2, CL3 drawn in the figure are partition lines for distinguishing the steel of the present invention from the conventional steel. The first critical marking line CL1 corresponds to a 0.2% yield strength σ of 600 MPa. The second critical marking line CL2 corresponds to the above formula (1). The third critical marking line CL3 corresponds to the above formula (2). A region R1 in the figure corresponds to a comparative example including a conventional example, and a region R2 corresponds to an example of the present invention.

(Comparative example)
Using a hot-rolled steel sheet having the chemical composition shown in Comparative Example 1 of Table 1 and performing cold rolling at a rolling rate of 30 to 70% and performing heat treatment at each temperature, the material hardness measurement and tensile test were 0. .2% yield strength σ and elongation ε were evaluated (FIGS. 3 and 4).

  FIG. 3 is a characteristic diagram showing the results of investigating the correlation between the various samples with the heating temperature (° C.) of the final heat treatment on the horizontal axis and the Vickers hardness Hv (load 1 kg) of various samples on the vertical axis. In the figure, the characteristic line F1 (white circle) indicates the rolling rate of 30%, the characteristic line F2 (white triangle) indicates the rolling rate of 50%, and the characteristic line F3 (white square) indicates the rolling rate of 70%. As is apparent from the figure, the material hardness changes abruptly from around 600 ° C., and the softening start temperature slightly changes depending on the rolling rate, but softening is almost completely completed at 700 ° C. at all rolling rates. .

  In FIG. 4, the horizontal axis indicates the heating temperature (° C.) of the final heat treatment, and the vertical axis indicates the tensile strength (MPa), 0.2% proof stress σ (MPa), elongation ε (%), and Vickers hardness Hv of various samples. It is a characteristic diagram which shows the result of having investigated (each load 1kg) about each correlation. The rolling rate was 70%. In the figure, the characteristic line M represents the tensile strength, the characteristic line N represents the 0.2% yield strength σ, the characteristic line P represents the Vickers hardness Hv, and the characteristic line Q represents the elongation ε. As is apparent from the figure, the ductility recovers with the heating temperature in the 70% rolled material, but the softening temperature is also remarkable, and the 0.2% proof stress decreases by 100 MPa or more at a temperature difference of 500 to 650 ° C. at 150 ° C. Therefore, the heating conditions for obtaining the quality stability as compared with Example 1 using the example steel to which Nb was added were in the temperature range of 400 to 600 ° C.

  In the steel type of Comparative Example 2, the same confirmation as in Comparative Example 1 was performed, and the heating conditions for obtaining stable quality were up to 600 ° C., and the mechanical property values (0.2% yield strength σ, elongation ε) and rolling at that time The mechanical properties as they are are shown as white square plots in FIG.

  The ferritic stainless steel sheet for molded springs of the present invention is used for various molded springs.

The characteristic line figure which shows the relationship between the heat processing temperature of Nb addition ferritic stainless steel sheet, and the raw material hardness after heat processing. The characteristic diagram which shows the relationship between the heat processing temperature of a Nb addition ferritic stainless steel plate, the tensile characteristic after heat processing, etc. FIG. The characteristic diagram which shows the relationship between the heat processing temperature of a Nb non-addition ferritic stainless steel plate, and the raw material hardness after heat processing. The characteristic diagram which shows the relationship between the heat processing temperature of a Nb non-addition ferritic stainless steel plate, the tensile characteristic after heat processing, etc. FIG. The characteristic plot figure which wrote together this invention and the prior art.

Claims (4)

In mass%, C: 0.03% or less, N: 0.03% or less, Si: 1.00% or less, Mn: 1.00% or less, Cr: 16 to 20%, Ni: 0.60% or less , Nb: Ferritic stainless steel containing 8 × (C + N)% or more and 0.80% or less, with the balance being Fe and inevitable impurities, and having a working strain equivalent to 15% or more of cold rolling inside And having a 0.2% proof stress σ of 600 MPa or more, and formula ε ≧ −0.02 × σ + 22 and formula ε ≧ 5. A ferritic stainless steel sheet for molded springs exhibiting an elongation ε (%) that satisfies the relationship 5 above. The ferritic stainless steel sheet for molded springs according to claim 1, further comprising one or two of Cu: 0.80% or less and Mo: 2.50% or less in mass%. In mass%, C: 0.03% or less, N: 0.03% or less, Si: 1.00% or less, Mn: 1.00% or less, Cr: 16 to 20%, Ni: 0.60% or less , Nb: 8 × (C + N)% or more and 0.80% or less respectively, and ferritic stainless steel with the balance being Fe and inevitable impurities, internal work strain equivalent to 15% or more of cold rolling Then, final heat treatment is performed in a temperature range of 550 to 750 ° C., 0.2% proof stress σ is 600 MPa or more, and elongation ε (%) is expressed by the formula ε ≧ −0.02 × σ + 22 and the formula ε ≧ 5. A method for producing a ferritic stainless steel sheet for molded springs, characterized in that the steel sheet satisfies the relationship 5 above. Furthermore, it contains 1 type or 2 types of Cu: 0.80% or less and Mo: 2.50% or less by mass%, The manufacture of the ferritic stainless steel plate for molded springs of Claim 3 characterized by the above-mentioned. Method.

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