JP2009203528A - Martensitic stainless steel for loom member having excellent corrosion resistance and wear resistance, and method for producing steel strip thereof - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a martensitic stainless steel for a loom member having excellent corrosion resistance and wear resistance, and to provide a method for producing a steel strip thereof. <P>SOLUTION: The martensitic stainless steel for a loom member having excellent corrosion resistance and wear resistance after quenching and tempering has a steel composition comprising, by mass, 0.20 to 0.30% C, 0.30 to 0.60% Si, ≤0.60% Mn, ≤0.035% P, ≤0.010% S, 15.0 to 16.6% Cr, 0.10 to 0.60% Ni, ≤0.50% Cu, ≤0.5% Mo, ≤0.10% V, ≤0.05% Nb, ≤0.05% Ti, ≤0.03% Al, 0.04 to 0.09% N, and the balance Fe with inevitable impurities, and satisfying C+N: 0.25 to 0.35%, C/N: 2.2 to 6.0 and Cr+3.3Mo: 15 to 16.6. <P>COPYRIGHT: (C)2009,JPO&INPIT

Description

  The present invention relates to a martensitic stainless steel excellent in corrosion resistance and wear resistance after quenching and tempering and a method for producing the steel strip. More specifically, the present invention relates to martensitic stainless steel for loom members such as flat healds, droppers, wings, deformed ridges, dents and reeds which have excellent corrosion resistance and wear resistance and have a long life.

  For weaving machine members such as flat healds, droppers, wings, deformed wrinkles, reeds, dents, etc., stainless steel SUS420J2 is tempered and tempered. Precipitation strengthened stainless steel is used. The background to the use of such high-strength materials is the phenomenon that the yarn path is worn by the yarn due to long-term specifications. Particularly in recent years, the wear environment has become severe due to the high functionality of fibers.

  Further, the reason why stainless steel having corrosion resistance is required is that it is difficult to prevent corrosion due to surface treatment such as painting or plating due to wear. Further, in a loom where a weft is blown by a water jet, corrosion is promoted due to a moist environment. Furthermore, in order to prevent water jet nozzle clogging, an aqueous sodium hypochlorite solution may be added, and there are cases in which loom parts corrode in a short period of time due to adhesion of chlorine ions. Moreover, in precipitation strengthened stainless steel in which carbonitrides are dispersed, a problem of forming comet-like wear marks on the yarn path and damaging the fibers is also recognized.

  The corrosion resistance of stainless steel is generally organized by component and is known to be improved by the addition of Cr, Mo, and N. Many studies have been made on the effect of each element, and in martensitic stainless steel, it is possible to organize by Cr + 3.3Mo + 16 to 30N, and there is a report that the corrosion resistance improves as this value increases. In addition, since stainless steel is used after being quenched, it is also necessary to improve polishing properties by avoiding large inclusions by lowering Al or the like.

  These findings are explained in the patent literature. First, in Patent Document 1, a high-strength martensite system excellent in weather resistance containing Cr: 12-16%, Mo: 1.3-3.5%, N: 0.06% -0.13% Stainless steel wire is described.

  Mo, which improves weather resistance, is an expensive element and has a problem of reducing hardenability by narrowing the austenite temperature range. If austenite cannot be converted into a single phase during quenching heat treatment, quenching starts from the two-phase region of austenite and ferrite. In this case, carbide precipitates from ferrite having a high C diffusion rate, and the resulting Cr-deficient layer significantly reduces the corrosion resistance. Of course, even in the austenite phase, if the cooling rate is slow, carbides are precipitated and the corrosion resistance is lowered. However, since the diffusion rate is smaller than in the ferrite, the influence of the cooling rate is relatively small. Such a decrease in corrosion resistance due to the precipitation of carbides becomes apparent when the cooling rate is slow, for example, when quenching is performed by gas cooling.

  On the other hand, nitrogen expands the austenite region and is an inexpensive element, but nitrogen exceeding the solid solubility limit at the time of melting and casting creates bubbles, and a problem is that a healthy steel ingot cannot be obtained. The solid solubility limit of nitrogen varies depending on the components and atmospheric pressure. The effects of Cr and C as components are large, and when martensitic stainless steels such as SUS420J1 and SUS420J2 are cast under atmospheric pressure, the amount of dissolved nitrogen is generally reported to be about 0.1%. Patent Document 2 also describes that N: 0.06 to 0.10% as martensitic stainless steel having no pinhole defect.

  As a martensitic stainless steel for loom parts, a steel type using precipitation strengthening of Ti and Nb is described in Patent Document 3. Ti + Nb: 0.05 to 2.0% in total amount is added to the matrix. It is described that the wear resistance is improved by dispersing and precipitating at a total precipitation amount of 1% or more.

  As described above, various martensitic stainless steels with improved corrosion resistance and martensitic stainless steels for loom parts with improved wear resistance have been proposed.

  However, as a result of studying the application of various martensitic stainless steels in the loom parts application by the present inventors, in Patent Document 1, the main focus is on improving the corrosion resistance by adding Cr and Mo. In order for the Cr and Mo concentrated sites due to solidification segregation to become stable δ-ferrite phase and to become austenite single phase, a long-time quenching heat treatment is required and hot-rolled sheet It has been found that there is a problem that a long time is required even in softening annealing performed before cold rolling.

  In addition, the method described in Patent Document 2, that is, adding 0.06% to 0.10% of nitrogen for improving corrosion resistance without causing pinhole defects was also performed in Patent Document 1. However, since the Cr content is as low as 12.5 to 14.5%, it has been found that sufficient corrosion resistance cannot be obtained in this environment. Further, in terms of wear resistance, C: 0.12 to 0.17% and the quenching hardness is low, so that it was also found that sufficient wear resistance cannot be obtained.

  Next, in the stainless steel described in Patent Document 3, since the main focus is on strengthening dispersion precipitation of carbonitrides, ferrite remains even after quenching, and a uniform quenched structure cannot be obtained. In addition, it has been found that sufficient corrosion resistance cannot be obtained when the corrosion resistance is reduced due to the undissolved carbonitride. Further, since coarse hard carbonitrides of Ti and Nb are dispersed, there is a problem that only the periphery of the carbonitride is worn unevenly, resulting in comet-like wear marks.

JP-A-5-287456 JP 2005-163176 A JP 2000-192198 A

  In view of the present situation described above, an object of the present invention is to provide a martensitic stainless steel sheet for loom parts that has good corrosion resistance after quenching and tempering and excellent wear resistance at low cost.

  In order to achieve the above object, the present inventors investigated the effects of martensitic stainless steel components and manufacturing conditions, quenching and tempering conditions on the corrosion resistance and wear resistance in the use environment of the loom parts. The effects of the precipitates after quenching and the wear resistance were examined. As a result, in order to obtain good corrosion resistance, it is important to increase the stability of austenite in the heating temperature range during quenching and to adjust the amount of carbonitride deposited during quenching, In particular, the inventors learned that it is very important to optimize the component balance of C, N, Cr, and Mo and reduce undissolved carbides. In particular, in the process of quenching and tempering thin stainless steel strips such as loom parts in a continuous line, in order to build optimum corrosion resistance and wear resistance, it is important to design the components suitable for that process. I found. The present invention has been made based on the above findings, and the gist thereof is as follows.

(1) By mass%, C: 0.20 to 0.30%, Si: 0.30 to 0.60%, Mn: 0.60% or less, P: 0.035% or less, S: 0.010 % Or less, Cr: 15.0 to 16.6%, Ni: 0.10 to 0.60%, Cu: 0.50% or less, Mo: 0.50% or less, V: 0.10% or less, Nb : 0.05% or less, Ti: 0.05% or less, Al: 0.03% or less, N: 0.04% or more and 0.09% or less, having a steel composition comprising the balance Fe and unavoidable impurities, C + N: 0.25 to 0.35%, C / N: 2.2 to 6.0, Cr + 3.3Mo: 15 to 16.6, corrosion resistance and wear resistance after quenching and tempering Excellent martensitic stainless steel for loom parts.

(2) The martensitic stainless steel described above is cold-rolled to 0.9 mm or less, subjected to solution treatment in a temperature range of 950 to 1100 ° C. for 5 to 180 seconds, and then cooled to 200 ° C. or less. Of the martensitic stainless steel strip for loom parts excellent in corrosion resistance and wear resistance after quenching and tempering, characterized by performing tempering for 5 to 300 seconds in a temperature range of 300 to 500. Production method.

  By optimizing the balance of each component of martensitic stainless steel, the corrosion resistance of the matrix after quenching and tempering is ensured, and at the same time, stainless steel that is wear resistant and optimal for loom parts is inexpensive. It became possible to provide.

  The present invention is described in detail below.

  In general, the corrosion resistance of stainless steel is arranged by its components, and is arranged by an index such as Cr + 3.3Mo + 16 to 30N. The higher this value, the higher the corrosion resistance. The corrosion resistance at this time refers to a neutral chloride aqueous solution environment. As an evaluation method, for example, a method for measuring the pitting potential of stainless steel defined in JIS G0577 or a salt spray test method defined in JISZ2371. Etc. are raised. SUS420J1 steel as a western tableware knife is extremely unlikely to be exposed to high-concentration chloride aqueous solutions in storage tanks such as chemical / food plants and water heaters, in applications other than those used in the beach environment, that is, in everyday indoor environments. As is used, sufficient corrosion resistance can be obtained even with an amount of Cr of about 13%.

  However, when a sodium hypochlorite aqueous solution is added to water in a water jet type loom, chlorine ions adhere, remain, and concentrate on the surface of the loom parts, particularly in the gap structure, and the 13Cr-based martensitic stainless steel In SUS420J1 or SUS420J2 steel, the corrosion resistance cannot be maintained. In the present invention, the Cr content is set to 15.0 to 16.5% or more and N: 0.04 to 0.09%, so that the corrosion resistance after quenching and tempering is sufficient in the usage environment of the loom parts. It can be secured.

  There are several points in the mechanism for improving the corrosion resistance of martensitic stainless steel according to the present invention. The first point is that weaving machine parts mainly have a thin plate thickness of 0.5 mm or less, so even with air-cooled quenching, compared to the cooling rate of stainless steel for western dishes knives with a plate thickness exceeding 6 mm, Although the cooling rate is relatively fast, if undissolved carbides remain, sensitization tends to be promoted. Therefore, the solution of carbide was promoted by lowering the C / N ratio with a constant amount of C + N. By increasing the amount of N, the corrosion resistance of the matrix is also improved, and carbide precipitation during cooling is suppressed.

  The second point of improving corrosion resistance is optimization of Cr content. Increasing the amount of Cr, Mo, N is effective to ensure sufficient corrosion resistance in the environment. However, the increase of Cr, Mo decreases the austenite single-phase temperature range in the solution treatment, and in some cases austenite From the two-phase structure of ferrite. Since sensitization in the ferrite phase occurs in a shorter time than austenite, in the production of a loom component premised on gas cooling, sensitization is promoted and corrosion resistance is greatly impaired. Therefore, it is important to define the upper limit for the amount of Cr and Mo, which are ferrite forming elements, and to control within the appropriate range.

  The third point of improving corrosion resistance is to perform a solution treatment in the austenite single phase region, and to perform tempering in a temperature region in which carbonitride does not precipitate during quenching. . By using a cold-rolled material, the solution of C and N is promoted, and even in the step of forming a steel strip in a short time of 120 seconds or less in a continuous annealing furnace, the amount of C and N is within the scope of the present invention. It became possible to make it fully solution.

  These corrosion resistance improving mechanisms have made it possible to obtain martensitic stainless steel having sufficient wear resistance and burn-out / tempering hardness as a loom part and having sufficient corrosion resistance in a loom environment.

  Based on the above knowledge, this invention discovered the optimal component balance as a martensitic stainless steel in the said use. The reasons for limiting each component will be described below. In the following description, “%” indicating the content of each element indicates “mass%” unless otherwise specified.

C: 0.20 to 0.30%
C is an element that controls the quenching hardness, and is required to be 0.20% or more in order to obtain the hardness required for the loom parts. On the other hand, if it is added excessively, the quenching hardness is increased more than necessary, the load during punching increases, and comet-like wear marks due to undissolved carbides also occur. Further, since Cr carbide precipitates during air cooling and the corrosion resistance is impaired, the content is set to 0.30% or less.

Si: 0.30 to 0.60%
Si is necessary for deoxidation at the time of melting and refining, and is also effective in suppressing the formation of oxide scale during the quenching heat treatment, so it was set to 0.30% or more. However, Si was made 0.60% or less in order to narrow the austenite single phase temperature range and impair quenching stability.

Mn: 0.60% or less Although Mn is an austenite stabilizing element, 0.60% was made the upper limit in order to promote the formation of an oxide film during quenching heat treatment and lower the subsequent corrosion resistance.

P: 0.035% or less P is an element contained as an impurity in a raw material alloy such as hot metal or ferrochrome. In addition to being harmful to hot-rolled annealed sheets and toughness after quenching, the corrosion resistance is deteriorated by the formation of δ ferrite accompanying solidification segregation, so the content was made 0.035% or less.

S: 0.010% or less S is an element that has a small amount of solid solution in the austenite phase and segregates at the grain boundaries to promote a decrease in hot workability. Therefore, it was made 0.010% or less.

Cr: 15.0 to 16.6%
Cr needs to be at least 15.0% in order to maintain sufficient corrosion resistance in the usage environment of the loom parts. On the other hand, since it has the effect of narrowing the austenite stable temperature range, the upper limit was made 16.6%. In order to make these characteristics more effective, the Cr range is preferably 15.2 to 15.7%.

Ni: 0.10 to 0.60%
Ni, as well as Mn, is an austenite stabilizing element and an element effective for improving toughness after quenching. Furthermore, since it is also effective in suppressing crevice corrosion, it was decided to add at least 0.10%. On the other hand, Ni is more expensive than other alloy elements, and is set to 0.60% or less in order to increase the cost.

Cu: 0.50% or less Cu is often inevitably contained, such as mixing from scrap during melting, but excessive content reduces hot workability and corrosion resistance, so 0.5% or less It was.

V: 0.10% or less V is often inevitably mixed from ferrochromium or the like, which is an alloy raw material.

Al: 0.03% or less Al is an element effective for deoxidation, but raises the basicity of the slag, precipitates soluble inclusions CaS in the steel, and lowers the corrosion resistance. Moreover, since it causes a decrease in abrasiveness due to alumina-based nonmetallic inclusions, the upper limit was set to 0.03%.

N: 0.04% to 0.09% N, like C, has the effect of increasing the quenching hardness. Further, as an effect different from C, the corrosion resistance is improved in the following two points. The first is to strengthen the passive film, and the other is to suppress the precipitation of Cr carbide (suppression of the Cr-deficient layer). In order to obtain these effects, N is set to 0.04% or more. However, excessive addition drastically reduces the amount of Cr carbide precipitated, impairs wear resistance, and impairs manufacturability, so 0.09% or less.

Ti: 0.05% or less Ti forms carbonitrides, and it is difficult to form a solution by solution treatment during quenching of the steel. In order to prevent uneven wear due to carbonitrides, the upper limit was made 0.050%.

Nb: 0.05% or less Nb is a carbonitride-forming element like Ti. In order to prevent uneven wear due to carbonitrides, the upper limit was made 0.050%.

  In the martensitic stainless steel described above, addition of Mo to the steel works effectively to further improve the corrosion resistance.

Mo: 0.50% or less In order to improve corrosion resistance, addition of Mo is effective, but it is an expensive element, and in the solution heat treatment temperature range during quenching, the austenite single phase temperature range is narrowed, In order to impair the insertability, the upper limit is made 0.50%.

  A desirable range of components can be obtained by satisfying the component conditions defined by the formula. The reason for the regulation will be explained below.

C + N: 0.25 to 0.35%
In order to obtain the quenching and tempering hardness required for the loom parts, the total amount of C + N is required to be 0.25% or more. However, when the amount of C + N becomes excessive, the quenching and tempering hardness increases and the punchability of the product is impaired, so 0.35% was made the upper limit.

C / N: 2.2 to 6.0
Regarding quenching hardness, C and N act substantially equivalently, but the effect differs with respect to corrosion resistance and wear resistance, so it is necessary to control the ratio of C and N. The C / N lower limit is set at 2.2 from the viewpoint of improving wear resistance. Moreover, the upper limit was set to 6.0 in order to improve corrosion resistance by sensitization and prevention of decarburized layer.

Cr + 3.3Mo: 15 to 16.6
Cr, Mo, and N are elements that are effective in improving the corrosion resistance. Since Cr and Mo have the same mechanism of action, 15% or more is required when the required corrosion resistance is arranged by the amount of Cr + 3.3Mo. . However, if Cr + 3.3Mo is raised excessively, the solution heat treatment temperature range is narrowed during quenching, so 16.6% is made the upper limit.

  FIG. 1 shows the relationship between the optimum range of C + N and C / N and the range defined for each of C and N, and FIG. 2 shows the relationship between Cr, Mo, N and the loom parts quality and manufacturability. Further, FIG. 3 shows the relationship between the thickness of the steel strip in the representative component system and the quality after quenching and tempering. Only when all the conditions that are the constituent requirements of the present invention are satisfied, it becomes possible to satisfy all of the corrosion resistance and wear resistance, quenching and tempering hardness, and manufacturability at the time of gas cooling and quenching. In FIG. 3, the ◯ mark indicates the pitting potential, and the △ mark indicates the quenching hardness. When the pitting potential exceeds 200 mV, no significant rust is observed even when evaluated for 3 weeks in the salt spray test, which is considered to have sufficient corrosion resistance in the loom environment. When the plate thickness exceeded 0.9 mm, the cooling rate in the vicinity of 650 ° C. became lower than 30 ° C./s in the continuous quenching equipment, and the corrosion resistance and hardness decreased due to sensitization.

  Next, in the production of martensitic stainless steel according to the present invention, the heating temperature during hot rolling is set to 1140 to 1240 ° C., the coiling temperature is set to 700 to 840 ° C., and hot rolled sheet annealing is performed in a batch annealing furnace. It is desirable to carry out at 700 to 900 ° C. for 4 hours or longer.

  That is, when the hot rolling heating temperature is higher than 1240 ° C., the two-phase region from γ single phase to γ + δ is obtained. In the δ phase, Cr, Si and the like are concentrated, and C, N, Ni and the like are segregated, hindering the γ single phase at the time of quenching and impairing the hardenability. On the other hand, when the temperature is lower than 1140 ° C., a soaking time of 2 hours or more is required as a diffusion time for eliminating the solidification segregation, which is not preferable because productivity of hot rolling is greatly impaired.

  In addition, when the steel strip is wound after hot rolling, the winding temperature is preferably set to 700 to 840 ° C. By setting it to 700 or more, the coarsening of the carbide effective for improving the wear resistance proceeds at the time of cooling the coil. On the other hand, when the temperature exceeds 840 ° C., a thick oxide scale is formed on the surface, which causes undesirable problems such as a decrease in corrosion resistance due to the formation of a decarburized phase and poor polishing properties after quenching.

  Next, although it is the annealing conditions of a hot-rolled sheet, in order to improve the workability before quenching, it is necessary to make it soft. For this purpose, since a continuous annealing furnace cannot secure an annealing time for sufficient softening, a heat treatment is preferably performed in a batch annealing furnace in a temperature range of 700 to 900 ° C. for 4 hours or more. Softening becomes insufficient at 700 ° C. or lower or 900 ° C. or higher. If the time is less than 4 hours, material variation in the coil due to temperature non-uniformity in the coil occurs.

  The hot-rolled steel sheet is cold-rolled after pickling. At this time, intermediate annealing or pickling is performed as necessary. Although this cold-rolled sheet is used for quenching, the use of the cold-rolled sheet can promote solution formation during quenching. In order to obtain a sufficient cooling rate in the gas, it is desirable that the plate thickness be 0.9 mm or less. When cold-rolled annealed sheets or cold-rolled sheets with a thickness of more than 0.9 mm are quenched in the same way as cold-rolled materials of 0.9 mm or less, corrosion resistance is reduced due to delayed solution and precipitation of carbides during cooling. And quenching hardness decreases. Solution treatment and quenching conditions suitable for cold-rolled annealed sheets and cold-rolled materials exceeding 0.9 mm in thickness can be used, but the equipment and operating costs increase.

  In the quenching heat treatment, it is desirable to hold for 5 to 120 seconds in a temperature range of 950 to 1100 ° C. and perform gas cooling quenching.

  In solution treatment, in order to obtain an austenite single phase structure in the steel type, 950 ° C. or higher is necessary. However, if the temperature exceeds 1100 ° C., the sheet passing property is impaired due to a decrease in high-temperature strength or the like, so that the temperature is 1100 ° C. or less. Further, the solution treatment time was set to 5 seconds or more for the austenite coal phase, similarly to the temperature, and was set to 300 seconds or less from the viewpoint of sheet passing.

  At the time of quenching, in order to almost complete the martensitic transformation with the steel of the present invention, it is necessary to set the temperature to 200 ° C. or lower. Further, the cooling rate during this period needs to be 20 ° C./second or more in order to suppress sensitization in the austenite phase.

  Following quenching, it is necessary to temper to improve toughness. In order to perform in a continuous annealing furnace, it is necessary to complete tempering in a short time, and for that purpose, 300 ° C. or higher is required. However, if the temperature is raised excessively, the corrosion resistance is impaired due to precipitation of carbides, so it is necessary to set the temperature to 500 ° C. or lower. In order to perform tempering stably in the temperature range, 5 seconds or more are required. Moreover, since tempering for a long time may impair the corrosion resistance, it should be 300 seconds or less.

  Steel having chemical composition values (mass%) shown in Table 1 and Table 2 (continued in Table 1) is melted in a vacuum melting furnace, and then cast in an inert gas nitrogen atmosphere at atmospheric pressure to give a steel having a thickness of 100 mm. It was made a lump. Then, after heating to 1220 ° C., it was hot-rolled to a plate thickness of 2.7 mm and wound up at 700 ° C. Subsequently, after heat treatment at 850 ° C. for 4 hours, the furnace was cooled and tempered. After pickling, it was cold-rolled to a thickness of 0.9 mm and softened and annealed at 750 ° C. Further, the sheet was cold-rolled to a thickness of 0.3 mm, held at 1050 ° C. for 120 seconds in a heat treatment furnace in a nitrogen atmosphere, then gas-cooled and quenched, and subsequently tempered at 400 ° C. for 60 seconds. Using the obtained quenched and tempered steel sheet as a test material, the quenching hardness, corrosion resistance, and wear resistance were evaluated by the following methods.

Based on the Vickers hardness test defined in JISZ2244, the thickness was measured at a load of 50 N in the thickness section of the hardness plate. Hv500 or more and 570 or less were set as the pass.

The surface of the sample after the corrosion-resistant quenching was sanded with a 600th abrasive finish. A salt spray test prescribed in JISZ2371 was conducted for 3 weeks, and a product with slight rusting or no rusting was regarded as acceptable.

The wear depth was measured by rubbing the wear- resistant specimen with a 10 mm diameter alumina ball. The load was 9.8 N, the sliding speed was 10 to 100 mm / s, the stroke was 20 mm, and the number of reciprocations was 500. The wear depth was 1.0 μm or less.

  As can be seen from the results shown in Table 3, the steel of the present invention satisfies the hardness range desired for the loom parts when quenched and tempered: Hv 500 to 570, and the occurrence of rust in the SST test is extremely small. In addition, it has excellent wear resistance and excellent quality.

  On the other hand, with components out of the scope of the present invention, quenching and tempering hardness and corrosion resistance are poor, or other characteristics (bubble-based defects, hot workability, raw material cost) are inferior to the invention steel. It was rejected in terms of manufacturability, quality, and cost.

  ADVANTAGE OF THE INVENTION According to this invention, it becomes possible to manufacture the martensitic stainless steel for loom members excellent in corrosion resistance and wear resistance when quenched and tempered by gas cooling at low cost and with high productivity. Therefore, the present invention contributes to greatly improving the production cost and quality of stainless steel for loom parts.

The figure which shows the optimal component range of C and N. FIG. The figure which shows the optimal component range of Cr, Mo, and N. The figure which shows the influence of board thickness with respect to corrosion resistance and abrasion resistance.

Claims (2)

  In mass%, C: 0.20 to 0.30%, Si: 0.30 to 0.60%, Mn: 0.60% or less, P: 0.035% or less, S: 0.010% or less, Cr: 15.0 to 16.6%, Ni: 0.10 to 0.60%, Cu: 0.50% or less, Mo: 0.50% or less, V: 0.10% or less, Nb: 0.0. 05% or less, Ti: 0.05% or less, Al: 0.03% or less, N: 0.04% or more and 0.09% or less, the steel composition consisting of the balance Fe and unavoidable impurities, C + N: 0 A loom excellent in corrosion resistance and wear resistance after quenching and tempering, characterized by being 25 to 0.35%, C / N: 2.2 to 6.0, and Cr + 3.3Mo: 15 to 16.6 Martensitic stainless steel for parts.   The martensitic stainless steel according to claim 1 is cold-rolled to 0.9 mm or less, subjected to solution treatment in a temperature range of 950 to 1100 ° C. for 5 to 180 seconds, and then rapidly cooled to 200 ° C. or less. Production of martensitic stainless steel strip for loom parts excellent in corrosion resistance and wear resistance after quenching and tempering, characterized by performing quenching and subsequently tempering for 5 to 300 seconds in a temperature range of 300 to 500 Method.

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