WO2014030607A1 - ステンレス鋼板とその製造方法 - Google Patents
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- 238000004519 manufacturing process Methods 0.000 title claims description 22
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
Definitions
- the present invention relates to an austenitic stainless steel sheet suitable for use in etching and a method for producing the same.
- This application claims priority based on Japanese Patent Application No. 2012-181628 for which it applied to Japan on August 20, 2012, and uses the content here.
- Etching is performed by masking a part of the metal plate with a photoresist method, etc., and then contacting the metal plate with an etching solution by spraying or dipping to melt the exposed part of the metal plate, thereby chemically treating the metal plate.
- This is a technology for molding.
- Etching is used to manufacture precision electronic parts such as shadow masks, encoder slits, and lead frames, and precision machine parts such as springs and gears.
- Etching is a technology that melts and removes unnecessary parts of the metal plate to form the target shape.
- the processing accuracy is low unless the etching surface is smooth.
- an etching material may be used for the exterior material, and if the etched surface is not smooth, color unevenness occurs and the design properties are greatly reduced.
- the etching material is used as a microreactor, there is an effect that the liquid flowing inside is hard to collect if the etching surface is smooth.
- Patent Document 1 discloses an austenite that suppresses crystal grain growth by performing annealing after the final cold rolling at a temperature lower than a normal temperature of 500 to 850 ° C., thereby improving the etching rate and ensuring the smoothness of the etched surface.
- Stainless steel has been proposed.
- a substance called “smut” (carbide remaining during etching) adheres to the etched surface due to precipitation of carbides, lowers the etching rate, and smoothes the etched surface by smut. There was a problem that the property was impaired.
- Patent Document 2 proposes a stainless steel plate for photoetching having an average crystal grain size of 15 ⁇ m or less and a smooth etched surface by adjusting the chemical composition and manufacturing process conditions.
- Patent Document 2 proposes a stainless steel plate for photoetching having an average crystal grain size of 15 ⁇ m or less and a smooth etched surface by adjusting the chemical composition and manufacturing process conditions.
- Patent Document 3 proposes a stainless steel for photoetching having an average crystal grain size of 10 ⁇ m or less by adjusting the chemical composition and manufacturing process conditions.
- Patent Document 3 since expensive V is added, the cost of the material is significantly increased.
- the smoothness of the etched surface was improved.
- the etching material is used as a paper feed gear of the printer, there still remains a problem that the printing paper is wrinkled or the ink adheres to the concave portion of the uneven surface and stains the printing paper. Further, there is no problem such as color unevenness of the etched surface in the exterior material.
- An object of the present invention is to provide industrially stable austenitic stainless steel capable of further smoothing the etching surface in view of the above-described current situation. Specifically, it is to provide an austenitic stainless steel sheet having excellent etching surface smoothness and a method for producing the same.
- the inventors paid attention to the etching property for each crystal grain regarding the problem that cannot be solved by the conventional technique.
- Etching is a technique in which the steel sheet surface is chemically dissolved and removed.
- the dissolution rate varies depending on the crystal orientation of the steel sheet in contact with the etching solution. In other words, since the dissolution rate differs for each crystal grain, the size of the unevenness on the etched surface is the same as that of the crystal grain.
- the etching surface of the steel sheet is a set of fine regions (fine crystal grains) having random crystal orientations.
- austenitic stainless steel consists of a metastable austenitic phase.
- the structure of austenitic stainless steel is refined by work-induced martensitic transformation by cold rolling and by reverse transformation to austenite by subsequent low-temperature annealing.
- low-temperature annealing is performed at a temperature of less than 700 ° C., for example, the crystal orientation is uniform (the crystal orientation is not random) as shown by the region surrounded by the dotted line in FIG. The area remains.
- Such a coarse region having a uniform crystal orientation is preferentially dissolved as compared with other portions during etching, or is hardly dissolved.
- the concave portion or convex portion of the etching surface becomes remarkably large. Even if such a remarkably large concave portion or convex portion is formed, the average roughness Ra indicating the smoothness of the surface may not be greatly changed, so that it has been conventionally overlooked.
- the average length RSm of the roughness curve elements is used as an evaluation of the coarse region where the crystal orientations are aligned. This value is an average value of the length of one concave portion and convex portion on the surface.
- the structure is a collection of fine crystal grains having no coarse region with uniform crystal orientation
- the etched surface is smooth (the unevenness and the interval between the unevenness are small).
- the “crystal grain” is defined as a region surrounded by a boundary having a crystal orientation difference of 15 ° or more.
- it has been found that it is effective to generate sufficient work-induced martensite by cold rolling before annealing.
- the ⁇ phase region remaining after the cold rolling is inherited by the structure after annealing as a coarse region having such a uniform crystal orientation.
- the work-induced martensite produced by cold rolling contains many strains, and therefore becomes fine ⁇ grains (recrystallized grains) by subsequent annealing. Furthermore, it was found that optimizing the chemical composition of the steel sheet is effective for producing a large amount of martensite by cold rolling.
- the present invention is as follows. [1] % By mass C: 0.03% or less, Si: 1.0% or less, Mn: 1.5% or less, Mo: 2.0% or less, Cr: 12.0% to 20.0%, Ni: 4.5% or more and 9.0% or less, Cu: 1.5% or less, N: 0.03% or more and 0.15% or less, Nb: 0.01% or more and 0.50% or less, The balance is Fe and impurities,
- the Md30 value represented by the following formula (1) is 20 ° C. or more and 60 ° C.
- the Ni equivalent represented by the following formula (2) is 9.5% or more
- the ratio of crystal boundaries having an inclination angle of 15 ° or more out of crystal boundaries having an inclination angle of 2 ° or more is 95% or more
- the average of crystal grains surrounded by the crystal boundary having an inclination angle of 15 ° or more An austenitic stainless steel sheet having a diameter of 5 ⁇ m or less.
- Md30 value (° C.) 497-462 (% C +% N) -9.2 (% Si) -8.1 (% Mn) -13.7 (% Cr) -20 (% Ni +% Cu) -18.
- Ni equivalent (%) % Ni + 30 (% C +% N) +0.5 (% Mn) Formula (2)
- % C is the C content (% by mass)
- % N is the N content (% by mass)
- % Si is the Si content (% by mass)
- % Mn Mn.
- the balance is Fe and impurities,
- annealing is a method of manufacturing a steel sheet
- the cold rolling is a multi-pass rolling, and each pass is performed at 35 ° C. or less, a rolling speed of 200 m / min or less, and a tension in the rolling direction of 30 kg / mm 2 or more,
- the total sheet thickness reduction rate in the cold rolling is 50% or more
- Ni equivalent (%) % Ni + 30 (% C +% N) +0.5 (% Mn)
- % C is the C content (% by mass)
- % N is the N content (% by mass)
- % Si is the Si content (% by mass)
- % Mn is Mn.
- Content (mass%),% Cr is Cr content (mass%),% Ni is Ni content (mass%),% Cu is Cu content (mass%),% Mo is Mo content Amount (mass%) is shown.
- temper rolling is performed after the annealing.
- FIG. 1A shows the case where the amount of work-induced martensite before annealing is 78%.
- FIG. 1B shows a case where the amount of work-induced martensite before annealing is 90%.
- FIG. 2 (a) shows lath-shaped martensite.
- FIG. 2 (b) shows cellular martensite.
- C is precipitated as coarse Cr carbide at the crystal grain boundary and causes smut generation during etching. Therefore, the content is preferably small. However, since it is an element that can increase the strength of the steel sheet at low cost, it may be contained in a range of 0.03% or less that does not adversely affect the smut. For applications where smoothness after etching is strictly required, 0.02% or less is desirable. C is bonded to Nb and precipitates as a fine Nb compound during annealing, and has the effect of suppressing crystal grain growth. Therefore, C is preferably contained in an amount of 0.001% or more.
- Si is used as a deoxidizing material during melting and contributes to strengthening of steel.
- Si content is excessively large, there is an adverse effect of decreasing the etching rate. Therefore, Si may be contained in a range of 1.0% or less. Preferably, it is 0.6% or less.
- Mn contributes to preventing brittle fracture during hot working and strengthening steel.
- Mn is a strong austenite-generating element, if the content is excessively large, there are few work-induced martensites generated during cold rolling, and fine crystal grains cannot be obtained by subsequent annealing. Therefore, you may contain Mn in 1.5% or less of range. Preferably, it is 1.2% or less. More preferably, it is less than 1.2%.
- Cr is a basic element of stainless steel, and is an element necessary for forming a metal oxide layer on the surface of the steel material and enhancing the corrosion resistance.
- Cr is a strong ferrite stabilizing element, if the content is too large, ⁇ ferrite is generated. This ⁇ ferrite deteriorates the hot workability of the material. Therefore, the Cr content is 12.0% or more and 20.0% or less. Preferably, it is 15.0% or more and 19.0% or less.
- Ni is an austenite generating element and is an element necessary for stably obtaining an austenite phase at room temperature. Therefore, the lower limit is set to 4.5%. However, when there is too much Ni content, an austenite phase will be stabilized too much and the process induction martensitic transformation at the time of cold rolling will be suppressed. Furthermore, Ni is an expensive element, and an increase in content causes a significant increase in cost. Therefore, the upper limit is set to 9.0%. Preferably, the content is 6.0% or more and 8.5% or less.
- Mo improves the corrosion resistance of the material. However, if the Mo content is excessively high, the etching property is hindered and the cost is increased. Therefore, you may contain Mo in 2.0% or less of range. Preferably, it is 1.0% or less. More preferably, it is 0.50% or less.
- Cu is an austenite-forming element and is an element capable of adjusting the stability of the austenite phase. If the Cu content is excessively large, it segregates at the grain boundaries during the production process. This grain boundary segregation significantly deteriorates hot workability and makes manufacture difficult. Therefore, you may contain an upper limit in 1.5% of range. Desirably, it is 1.0% or less.
- N is a solid solution strengthening element like C and contributes to improving the strength of steel. Moreover, since it has the effect which couple
- Nb generates fine carbides or nitrides and suppresses crystal grain growth by a pinning effect. In other words, it is an element effective for refinement of crystal grains. Therefore, Nb is contained 0.01% or more. However, if the Nb content is too large, recrystallization is suppressed, and there is an adverse effect that a large amount of unrecrystallized portions remain after annealing. In addition, the addition of a large amount of Nb directly increases the cost of the material. Therefore, the upper limit is 0.50%. Preferably, the content is 0.02% or more and 0.20% or less.
- the chemical composition of the steel according to the present invention is further configured to contain each element in such a range that the following Md30 value and Ni equivalent satisfy the amounts specified below, with the balance being Fe and impurities. is there.
- Md30 value is an index of the ease with which processing-induced martensite is generated, represented by the formula (1). Qualitatively, if the Md30 value is large, work-induced martensite is likely to be generated during cold rolling. As described above, in order to change the metal structure at the time of annealing to a fine-grained austenite structure, 90% or more of the metal structure after cold rolling before annealing needs to be work-induced martensite. For that purpose, Md30 value shall be 20 degreeC or more. However, if the Md30 value is too large, the amount of work-induced martensite is excessively increased in the production process, and the rolling efficiency is remarkably deteriorated. Therefore, the upper limit value is set to 60 ° C.
- the temperature is 30 ° C. or higher and 50 ° C. or lower.
- Md30 value (° C.) 497-462 (% C +% N) -9.2 (% Si) -8.1 (% Mn) -13.7 (% Cr) -20 (% Ni +% Cu) -18. 5 (% Mo)
- Ni equivalent is an index indicating the stability of the austenite phase during annealing, which is represented by the following formula (2). Qualitatively, when the Ni equivalent is high, the austenite phase becomes stable. In order to reversely transform the work-induced martensite generated by cold rolling into an austenite phase during annealing, the Ni equivalent needs to be 9.5% or more. Desirably, it is 9.8% or more.
- Ni equivalent (%) % Ni + 30 (% C +% N) +0.5 (% Mn) Formula (2)
- % C is the C content (% by mass)
- % N is the N content (% by mass)
- % Si is the Si content (% by mass)
- % Mn is Mn.
- the ratio of the crystal boundary having the tilt angle (orientation difference) of 15 ° or more is defined as 95% or more.
- the ratio of the crystal boundary is the ratio to the crystal boundary having an inclination angle (orientation difference) of 2 ° or more.
- the “tilt angle” refers to the difference in angle between the crystal orientations (axes) of two adjacent crystals at the crystal boundary (that is, the grain boundary). Qualitatively, the smaller the tilt angle, the more adjacent crystal grains Will face in the same direction.
- the ratio of crystal boundaries having a small “tilt angle” is large, it becomes easy to form a coarse region in which crystal grains having a uniform crystal orientation are gathered, as shown in FIG.
- the ratio of crystal boundaries having a large “tilt angle” is large, the crystal orientation of each crystal grain is scattered, and the etching surface becomes smooth when etching is performed. See FIG. 1 (b).
- the tilt angle is measured by EBSP
- the tilt angles are indicated by colors, and this can be obtained by using a line segment method.
- the coarse region where the crystal grains having the same crystal orientation are gathered is selectively dissolved or difficult to dissolve only in that portion. Becomes larger.
- the etched surface becomes smooth as the ratio of crystal boundaries that greatly differ in the orientation difference between adjacent crystals increases.
- the ratio of crystal boundaries having an inclination angle of 15 ° or more among the crystal boundaries having an inclination angle of 2 ° or more is set to 95% or more.
- Average crystal grain size When the average crystal grain size decreases, the roughness of the etched surface decreases. Since this effect is particularly remarkable when the average crystal grain size is 5 ⁇ m or less, the average crystal grain size is set to 5 ⁇ m. In order to further exhibit the effect, the thickness is desirably 3 ⁇ m or less.
- a crystal boundary is defined as a boundary having a crystal orientation difference of 15 ° or more
- an average crystal grain size is defined as an average grain size of crystal grains surrounded by a boundary having such a crystal orientation difference of 15 ° or more. Is done.
- the average crystal grain size is calculated by the quadrature method from the EBSP orientation difference map at the center of the plate thickness.
- the manufacturing method of the stainless steel plate for etching according to the present invention will be described. You may carry out by the method similar to the past until hot rolling.
- the desired effect is exhibited by defining the annealing conditions as the final finishing process and the operating conditions of the cold rolling performed prior to the annealing. There are no special restrictions except for cold rolling and subsequent annealing.
- the ratio of boundaries having an inclination angle of 15 ° or more is 95% or more, and these boundaries (grain boundaries). It is important that the average diameter of the crystal grains surrounded by is set to 5 ⁇ m or less. If there is a coarse region in which ⁇ -grain nuclei are not formed during the final annealing, the region remains as a coarse region in which crystal grains divided by only a small inclination angle are aggregated even after annealing. In other words, the ⁇ -grain nuclei are simultaneously distributed and generated at the time of final annealing, so that these grains suppress each other's grain growth, and the above-described texture with excellent smoothness of the etched surface is obtained.
- ⁇ -grain nuclei generate defects such as grain boundaries and dislocations in the parent phase as sites. Since the work-induced martensite phase contains more dislocations than the austenite phase, it is effective to produce a large amount of work-induced martensite during cold rolling.
- the work-induced martensite produced by cold rolling is usually flat and elongated lath martensite as shown in FIG.
- This lath boundary also works effectively as a ⁇ grain nucleation site.
- this work-induced martensite is a cell-like martensite in which the lath is further divided into a plurality of pieces as shown in FIG. 2 (b)
- the boundary of this cell also becomes a nucleation site of ⁇ grains, and at the time of final annealing. Nuclei of ⁇ grains can be generated simultaneously and at many more locations.
- the cooling before the final annealing is performed. It is important how many cellular martensites are generated by hot rolling.
- ⁇ ′ processing induced martensite generated during cold rolling increases as the rolling reduction (sheet thickness reduction rate) increases.
- the cold rolling is a multiple pass rolling, each pass is 35 ° C. or less, the rolling speed is 200 m / min or less, and the tension in the rolling direction is 30 kg / mm 2 or more.
- the total sheet thickness reduction rate in cold rolling is set to 50% or more.
- the rolling start temperature is 35 ° C. or lower in all cold rolling passes.
- the control of the rolling start temperature is largely achieved in two ways.
- One is to suppress the heat generation itself in cold rolling. For that purpose, it is effective to use cold rolling as multiple pass rolling and reduce the rolling reduction per pass. Specifically, it is desirable that the rolling reduction rate of each pass is at most 20%.
- the other is a method of sufficiently cooling the plate after each pass.
- the rolling speed is preferably 200 m / min or less, more preferably 180 m / min or less. Furthermore, it is effective to allow a sufficient cooling time between the passes until the plate becomes 35 ° C. or lower. In the case of lever rolling, it is effective to remove the coil from the rolling mill and perform rolling after cooling.
- tension is applied in the rolling direction by the take-up reel.
- this tension is set to 30 kg / mm 2 or more, and more desirably 40 kg / mm 2 or more
- the compressive stress in the thickness direction due to rolling and the tensile stress in the length direction of the plate due to the tension of the reel are combined to generate a large number of slips.
- the band By activating the band, a large strain is given to the steel sheet, and a large amount of cellular martensite can be generated.
- the applied strain becomes uniform in the thickness direction by applying the tensile stress.
- the tension the friction between the plate and the roll during rolling is reduced, so that there is an effect of suppressing heat generation during rolling.
- the tension at the time of cold rolling is too large, there is a problem of an edge crack at the end of the rolled steel sheet or a plate breakage, and it is general that the tension is less than 30 kg / mm 2 .
- the C amount is set to 0.03% or less, ductility is ensured, and rolling can be performed with a tension of 30 kg / mm 2 or more.
- the annealing temperature is set to 950 ° C. or lower in order to suppress grain growth. However, if the annealing temperature is too low, many unrecrystallized parts remain, so the lower limit is set to 700 ° C.
- the annealing time is 2 to 300 seconds as the soaking time (time for maintaining at a predetermined temperature), and usually about 30 to 120 seconds is sufficient.
- a fine ⁇ grain structure with few unrecrystallized parts may be formed, and then temper rolling may be performed for performance adjustment such as hardness.
- temper rolling may be performed for performance adjustment such as hardness.
- processing-induced martensite is generated, but since this martensite is generated in units of the original ⁇ grains or smaller areas, the processing-induced martensite generated from fine ⁇ grains is fine. To be distributed. Therefore, the etched surface becomes smooth as before temper rolling.
- the temper rolling does not disperse the martensite region, and martensite with a similar orientation is generated as a lump. The smoothness of the surface is impaired.
- Table 1 shows the chemical composition of the test steel. Among the components, those outside the scope of the present invention are indicated by underlining the content numbers.
- a to E are chemical compositions that satisfy the definition of the present invention
- F to L are comparative chemical compositions that do not satisfy the specification.
- Percentage of crystal boundaries having an inclination angle of 15 ° or more After cutting, embedding and polishing a cross section perpendicular to the rolling direction, an EBSP orientation difference map was measured. A crystal boundary having an inclination angle of 2 to less than 15 ° and a crystal boundary having an inclination angle of 15 ° or more were distinguished, and the ratio of the crystal boundary having an inclination angle of 15 ° or more in the total boundary length was calculated.
- the crystal grain boundary was defined as a boundary where the inclination angle of adjacent crystal grains was 15 ° or more, and the average crystal grain size was calculated by the quadrature method from the EBSP orientation difference map at the center of the plate thickness.
- Presence / absence of Cr carbide After the surface of the test material was cut by 10 ⁇ m by chemical polishing, the diffraction peak was measured with an X-ray diffractometer. The characteristic X-ray was Co—K ⁇ ray, and the 2 ⁇ range was 20 to 100 °. The case where the Cr 23 C 6 and Cr 7 C 3 diffraction peaks were present was Cr carbide, and the case where the same peak was not confirmed was Cr carbide free.
- Etching surface roughness A specimen cut to a length of 20 mm was immersed in an etching solution for 600 s.
- the etching solution was a ferric chloride solution (specific gravity: 1.41) having a liquid temperature of 40 ° C.
- the average roughness Ra of the surface of the test material after immersion and the average length RSm (roughness interval) of the roughness curve element were measured with a laser microscope.
- the measurement area of the average roughness Ra was a surface of 100 ⁇ m ⁇ 100 ⁇ m, and the average value of the measurement results for each of the three specimens was taken as the measurement value.
- the measurement area of the average length RSm of the roughness curve element was a 200 ⁇ m line, and the average value of the measurement results for each of the three specimens was taken as the measurement value.
- Steel plates 1 to 6 in Table 2 satisfy the requirements of the present invention and have excellent etched surface roughness.
- Steel plates 7 to 17 are comparative steel plates and have poor etched surfaces. Although the steel plates 7 to 10 satisfy the requirements of the present invention, the etched surfaces are inferior in roughness because the ratio of the boundary at an inclination angle of 15 ° or more is small.
- the comparative steels 11 to 17 have a composition that does not satisfy the requirements of the present invention, and the etched surface is poor in roughness.
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Abstract
Description
[1]
質量%で、
C:0.03%以下、
Si:1.0%以下、
Mn:1.5%以下、
Mo:2.0%以下、
Cr:12.0%以上20.0%以下、
Ni:4.5%以上9.0%以下、
Cu:1.5%以下、
N:0.03%以上0.15%以下、
Nb:0.01%以上0.50%以下、
残部がFe及び不純物であり、
下記の式(1)で示すMd30値が20℃以上60℃以下、下記の式(2)で示すNi当量が9.5%以上であり、
金属組織において、2°以上の傾角を持つ結晶境界のうち、15°以上の傾角をもつ結晶境界の割合が95%以上であり、15°以上の傾角をもつ結晶境界で囲まれる結晶粒の平均直径が5μm以下である、オーステナイト系ステンレス鋼板。
Md30値(℃)=497-462(%C+%N)-9.2(%Si)-8.1(%Mn)-13.7(%Cr)-20(%Ni+%Cu)-18.5(%Mo) ・・・ 式(1)
Ni当量(%)=%Ni+30(%C+%N)+0.5(%Mn) ・・・ 式(2)
式(1)、(2)において、%CはCの含有量(質量%)、%NはNの含有量(質量%)、%SiはSiの含有量(質量%)、%MnはMnの含有量(質量%)、%CrはCrの含有量(質量%)、%NiはNiの含有量(質量%)、%CuはCuの含有量(質量%)、%MoはMoの含有量(質量%)を示す。
[1]のステンレス鋼板に調質圧延を施したオーステナイト系ステンレス鋼板。
質量%で、
C:0.03%以下、
Si:1.0%以下、
Mn:1.5%以下、
Mo:2.0%以下、
Cr:12.0%以上20.0%以下、
Ni:4.5%以上9.0%以下、
Cu:1.5%以下、
N:0.03%以上0.15%以下、
Nb:0.01%以上0.50%以下、
残部がFe及び不純物であり、
下記の式(1)で示すMd30値が20℃以上60℃以下、下記の式(2)で示すNi当量が9.5%以上である鋼片を、熱間圧延と冷間圧延を行った後、焼鈍して鋼板を製造する方法であって、
前記冷間圧延を複数パス圧延とし、かつ、各パスを35℃以下、圧延速度200m/min以下、圧延方向の張力30kg/mm2以上で行い、
前記冷間圧延における総板厚減少率を50%以上とし、
前記焼鈍を、700℃以上950℃以下の温度とする、オーステナイト系ステンレス鋼板の製造方法。
Md30値(℃)=497-462(%C+%N)-9.2(%Si)-8.1(%Mn)-13.7(%Cr)-20(%Ni+%Cu)-18.5(%Mo) ・・・ 式(1)
Ni当量(%)=%Ni+30(%C+%N)+0.5(%Mn) ・・・ 式(2)
式(1)、(2)において、%CはCの含有量(質量%)、%NはNの含有量(質量%)、%SiはSiの含有量(質量%)、%MnはMnの含有量(質量%)、%CrはCrの含有量(質量%)、%NiはNiの含有量(質量%)、%CuはCuの含有量(質量%)、%MoはMoの含有量(質量%)を示す。
[4]
[3]の製造方法において、前記焼鈍後に調質圧延を施す。
Md30値(℃)=497-462(%C+%N)-9.2(%Si)-8.1(%Mn)-13.7(%Cr)-20(%Ni+%Cu)-18.5(%Mo) ・・・ 式(1)
Ni当量(%)=%Ni+30(%C+%N)+0.5(%Mn) ・・・式 (2)
式(1)、(2)において、%CはCの含有量(質量%)、%NはNの含有量(質量%)、%SiはSiの含有量(質量%)、%MnはMnの含有量(質量%)、%CrはCrの含有量(質量%)、%NiはNiの含有量(質量%)、%CuはCuの含有量(質量%)、%MoはMoの含有量(質量%)を示す。
本発明では、2°以上の傾角(方位差)を持つ結晶境界のうち、15°以上の傾角(方位差)をもつ結晶境界の割合が95%以上と規定する。以下、特に規定しない場合でも、結晶境界の割合は2°以上の傾角(方位差)を持つ結晶境界に対する割合である。
Claims (4)
- 質量%で、
C:0.03%以下、
Si:1.0%以下、
Mn:1.5%以下、
Mo:2.0%以下、
Cr:12.0%以上20.0%以下、
Ni:4.5%以上9.0%以下、
Cu:1.5%以下、
N:0.03%以上0.15%以下、
Nb:0.01%以上0.50%以下、
残部がFe及び不純物であり、
下記の式(1)で示すMd30値が20℃以上60℃以下、下記の式(2)で示すNi当量が9.5%以上であり、
金属組織において、2°以上の傾角を持つ結晶境界のうち、15°以上の傾角をもつ結晶境界の割合が95%以上であり、15°以上の傾角をもつ結晶境界で囲まれる結晶粒の平均直径が5μm以下である、オーステナイト系ステンレス鋼板。
Md30値(℃)=497-462(%C+%N)-9.2(%Si)-8.1(%Mn)-13.7(%Cr)-20(%Ni+%Cu)-18.5(%Mo) ・・・ 式(1)
Ni当量(%)=%Ni+30(%C+%N)+0.5(%Mn) ・・・ 式(2)
式(1)、(2)において、%CはCの含有量(質量%)、%NはNの含有量(質量%)、%SiはSiの含有量(質量%)、%MnはMnの含有量(質量%)、%CrはCrの含有量(質量%)、%NiはNiの含有量(質量%)、%CuはCuの含有量(質量%)、%MoはMoの含有量(質量%)を示す。 - 請求項1記載のステンレス鋼板に調質圧延を施したオーステナイト系ステンレス鋼板。
- 質量%で、
C:0.03%以下、
Si:1.0%以下、
Mn:1.5%以下、
Mo:2.0%以下、
Cr:12.0%以上20.0%以下、
Ni:4.5%以上9.0%以下、
Cu:1.5%以下、
N:0.03%以上0.15%以下、
Nb:0.01%以上0.50%以下、
残部がFe及び不純物であり、
下記の式(1)で示すMd30値が20℃以上60℃以下、下記の式(2)で示すNi当量が9.5%以上である鋼片を、熱間圧延と冷間圧延を行った後、焼鈍して鋼板を製造する方法であって、
前記冷間圧延を複数パス圧延とし、かつ、各パスを35℃以下、圧延速度200m/min以下、圧延方向の張力30kg/mm2以上で行い、
前記冷間圧延における総板厚減少率を50%以上とし、
前記焼鈍を、700℃以上950℃以下の温度とする、オーステナイト系ステンレス鋼板の製造方法。
Md30値(℃)=497-462(%C+%N)-9.2(%Si)-8.1(%Mn)-13.7(%Cr)-20(%Ni+%Cu)-18.5(%Mo) ・・・ 式(1)
Ni当量(%)=%Ni+30(%C+%N)+0.5(%Mn) ・・・ 式(2)
式(1)、(2)において、%CはCの含有量(質量%)、%NはNの含有量(質量%)、%SiはSiの含有量(質量%)、%MnはMnの含有量(質量%)、%CrはCrの含有量(質量%)、%NiはNiの含有量(質量%)、%CuはCuの含有量(質量%)、%MoはMoの含有量(質量%)を示す。 - 請求項3に記載の製造方法において、前記焼鈍後に調質圧延を施す。
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WO2016047734A1 (ja) * | 2014-09-25 | 2016-03-31 | 新日鐵住金株式会社 | オーステナイト系ステンレス鋼板およびその製造方法 |
KR20170056007A (ko) * | 2014-09-17 | 2017-05-22 | 신닛테츠스미킨 카부시키카이샤 | 오스테나이트계 스테인리스 강판 |
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