JP5655385B2 - Ferritic stainless steel sheet with excellent ridging resistance and method for producing the same - Google Patents
Ferritic stainless steel sheet with excellent ridging resistance and method for producing the same Download PDFInfo
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- 229910001220 stainless steel Inorganic materials 0.000 title claims description 26
- 238000004519 manufacturing process Methods 0.000 title claims description 13
- 238000000137 annealing Methods 0.000 claims description 48
- 229910000859 α-Fe Inorganic materials 0.000 claims description 33
- 229910000831 Steel Inorganic materials 0.000 claims description 28
- 239000010959 steel Substances 0.000 claims description 28
- 238000005097 cold rolling Methods 0.000 claims description 12
- 229910052757 nitrogen Inorganic materials 0.000 claims description 8
- 229910052799 carbon Inorganic materials 0.000 claims description 7
- 239000000463 material Substances 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 6
- 229910052726 zirconium Inorganic materials 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims description 4
- 238000005554 pickling Methods 0.000 claims description 4
- 229910052717 sulfur Inorganic materials 0.000 claims description 4
- 238000009628 steelmaking Methods 0.000 claims description 2
- 239000013078 crystal Substances 0.000 description 27
- 238000005096 rolling process Methods 0.000 description 20
- 238000005260 corrosion Methods 0.000 description 15
- 230000007797 corrosion Effects 0.000 description 15
- 238000000034 method Methods 0.000 description 12
- 238000001953 recrystallisation Methods 0.000 description 10
- 230000007423 decrease Effects 0.000 description 7
- 238000005098 hot rolling Methods 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 239000000203 mixture Substances 0.000 description 4
- 230000001737 promoting effect Effects 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 239000004566 building material Substances 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 239000010960 cold rolled steel Substances 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 238000003756 stirring Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000000593 degrading effect Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 229910001651 emery Inorganic materials 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
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- 238000009864 tensile test Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
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Description
本発明は、耐リジング特性に優れたフェライト系ステンレス鋼板およびその製造方法に関するものである。 The present invention relates to a ferritic stainless steel sheet having excellent ridging resistance and a method for producing the same.
フェライト系ステンレス鋼板は、オーステナイト系ステンレス鋼板に比較して安価な材料であり、耐食性に優れていることから、建築材料、輸送機器、家庭電化製品、厨房機器等の様々な用途に使用されている。しかし、フェライト系ステンレス鋼は、加工の際にリジングと呼ばれる表面凹凸が発生しやすいという問題点を有している。 Ferritic stainless steel sheets are cheaper materials than austenitic stainless steel sheets and have excellent corrosion resistance, so they are used in various applications such as building materials, transportation equipment, home appliances, and kitchen equipment. . However, ferritic stainless steel has a problem that surface irregularities called ridging are likely to occur during processing.
リジング現象は、類似な結晶方位を有する冷延鋼板のフェライト粒の集合体（以下、コロニーと呼ぶ。）に起因し、その起源はスラブ凝固時に形成される粗大な柱状晶組織と考えられている。すなわち、粗大な柱状晶組織が、熱間圧延とそれに続く熱延板焼鈍後にも粗大なフェライト粒として残存し、冷間圧延、それに続く仕上焼鈍後に結晶方位の分散が小さい再結晶フェライト粒のコロニーを形成する。 The ridging phenomenon is caused by aggregates of ferrite grains (hereinafter referred to as colonies) of cold-rolled steel sheets having similar crystal orientations, and the origin is considered to be a coarse columnar crystal structure formed during slab solidification. . That is, a coarse columnar crystal structure remains as coarse ferrite grains after hot rolling and subsequent hot-rolled sheet annealing, and a colony of recrystallized ferrite grains with small dispersion of crystal orientation after cold rolling and subsequent finish annealing. Form.
このような仕上焼鈍後のコロニーの形成を抑制して耐リジング特性を改善するために、これまで数多くの技術が報告されている。主な技術として、（ａ）スラブ組織の高等軸晶率化、（ｂ）熱延板再結晶の促進、（ｃ）冷延板再結晶の促進が挙げられる。 Many techniques have been reported so far in order to improve the ridging resistance by suppressing the formation of colonies after such finish annealing. The main techniques include (a) increasing the equiaxed crystal ratio of the slab structure, (b) promoting hot-rolled sheet recrystallization, and (c) promoting cold-rolled sheet recrystallization.
（ａ）スラブ組織の高等軸晶率化技術として、特許文献１には、フェライト系ステンレス鋼スラブの連続鋳造時の電磁攪拌推力を４５〜１３０ｍｍＨｄとして電磁攪拌することでリジングの原因となる柱状晶の伸長肥大化を防止する技術が開示されている。 (A) As a technology for increasing the equiaxed crystal ratio of a slab structure, Patent Document 1 discloses a columnar crystal that causes ridging by electromagnetic stirring with an electromagnetic stirring thrust of 45 to 130 mmHd during continuous casting of a ferritic stainless steel slab. A technique for preventing the enlargement and enlargement of the skin is disclosed.
（ｂ）熱延板再結晶の促進技術として、特許文献２には、フェライト系ステンレス鋼鋼片の熱間圧延にあたり、その粗圧延段階の圧延に際し、前記粗圧延の最終パスの圧下率とその前のパスの圧下率との合計値を７０％以上、前記粗圧延の最終パス出側の圧延速度を２００ｍ／ｍｉｎ以上とし、前記粗圧延の仕上げ温度を１１００〜８００℃とすることを特徴とする耐リジング性に優れるフェライト系ステンレス鋼板の製造方法が開示されている。 (B) As a technique for promoting hot-rolled sheet recrystallization, Patent Document 2 describes the rolling reduction of the final pass of the rough rolling and the rolling ratio in the rolling of the rough rolling stage in hot rolling of ferritic stainless steel pieces. The total value with the rolling reduction of the previous pass is 70% or more, the rolling speed on the final pass exit side of the rough rolling is 200 m / min or more, and the finishing temperature of the rough rolling is 1100 to 800 ° C. A method for producing a ferritic stainless steel sheet having excellent ridging resistance is disclosed.
（ｃ）冷延板再結晶の促進技術として、特許文献３には、Ａｌ：０．０８〜０．５質量％を含有するフェライト系ステンレス鋼材を熱間圧延して熱延鋼板とし、該熱延鋼板を焼鈍することなくワ−クロ−ル径３００ｍｍφ以上の冷間圧延機で圧下率４０％以上の冷間圧延を施して冷延鋼板とし、次いで該冷延鋼板を７００〜１０５０℃の温度範囲で１０分間以内の中間焼鈍を行った後、更に４０％以上の圧下率で冷間圧延し、仕上焼鈍することを特徴とする表面性状及び加工性のすぐれたフェライト系ステンレス鋼板の製造法が開示されている。 (C) As a technique for promoting cold-rolled sheet recrystallization, Patent Document 3 discloses that a ferritic stainless steel material containing Al: 0.08 to 0.5% by mass is hot-rolled to form a hot-rolled steel sheet. A cold rolled steel sheet is subjected to cold rolling at a rolling reduction of 40% or more with a cold rolling mill having a work diameter of 300 mmφ or more without annealing the rolled steel sheet, and the cold rolled steel sheet is then heated to a temperature of 700 to 1050 ° C. A method for producing a ferritic stainless steel sheet having excellent surface properties and workability is characterized in that after intermediate annealing within 10 minutes in a range, cold rolling is further performed at a reduction rate of 40% or more, and finish annealing is performed. It is disclosed.
特許文献１に開示された技術では、凝固組織の微細化、等軸晶化に電磁攪拌は有効であるが、そのための高額な設備投資が必要となる。 In the technique disclosed in Patent Document 1, electromagnetic stirring is effective for refining the solidification structure and equiaxed crystallization, but it requires expensive capital investment.
また、特許文献２に開示された技術では、熱延中の再結晶および熱延板焼鈍中の再結晶促進に粗圧延の強圧下による熱延歪の増大は効果的である。しかし、Ｃｒを多く含有するフェライト系ステンレス鋼では、耐酸化性が良好であるため、表面に生成するスケールが薄く、圧延ロールとの焼き付きによる表面疵、いわゆる肌荒れが生じやすいという問題がある。熱延板に肌荒れが生じると、酸洗で溶解量を増やすために通板速度を低速にする必要が生じたり、さらにひどい場合には、熱延板の表面をグラインダー等により削る必要が生じるため、生産性・経済性が著しく低下するという問題もある。 Further, in the technique disclosed in Patent Document 2, it is effective to increase hot rolling strain due to strong rolling during rough rolling to promote recrystallization during hot rolling and recrystallization during hot rolling sheet annealing. However, since ferritic stainless steel containing a large amount of Cr has good oxidation resistance, there is a problem that the scale generated on the surface is thin, and surface flaws due to seizure with the rolling roll, so-called rough skin, are likely to occur. If the hot-rolled sheet becomes rough, it may be necessary to reduce the sheet-feeding speed to increase the amount of dissolution by pickling, or in severe cases it will be necessary to cut the surface of the hot-rolled sheet with a grinder or the like. There is also a problem that productivity and economy are significantly reduced.
特許文献３に開示された技術では、冷間圧延回数を増やして仕上焼鈍板の再結晶を促進することは効果的であるが、通常の冷延1回の製造法に比べて、中間焼鈍および冷間圧延の工程が増えることにより、大幅に生産性が低下するという問題がある。 In the technique disclosed in Patent Document 3, it is effective to increase the number of cold rolling and promote recrystallization of the finish annealed plate, but compared with the ordinary cold rolling one manufacturing method, intermediate annealing and As the number of cold rolling processes increases, there is a problem that productivity is significantly reduced.
本発明は、上記問題点に鑑み、安価かつ高効率な生産が可能な、耐リジング特性に優れたフェライト系ステンレス鋼板およびその製造方法を提供することを目的とする。 In view of the above problems, an object of the present invention is to provide a ferritic stainless steel sheet having excellent ridging resistance that can be produced at low cost and with high efficiency, and a method for producing the same.
本発明者らは、高額な鋳造設備の導入や生産性の低下を招くことなく製造できる耐リジング特性に優れたフェライト系ステンレス鋼板について鋭意検討を行った結果、
（１）仕上焼鈍板のフェライト粒の平均結晶粒径を１５μｍ以下に制御すれば、優れた耐リジング特性が得られること、
（２）仕上焼鈍板の微細な組織制御は、適量のＺｒの添加と仕上焼鈍温度の制御により得られ、特殊な鋳造条件や熱延条件、更には冷延回数の増加等は不要であることを知見した。
As a result of earnestly examining the ferritic stainless steel sheet excellent in ridging resistance that can be produced without introducing expensive casting equipment and reducing productivity,
(1) By controlling the average grain size of ferrite grains of the finish annealed plate to 15 μm or less, excellent ridging resistance can be obtained,
(2) Fine structure control of the finish annealed plate can be obtained by adding an appropriate amount of Zr and controlling the finish annealing temperature, and there is no need for special casting conditions, hot rolling conditions, or an increase in the number of cold rolling. I found out.
本発明は、このような知見に基づきなされたもので、その要旨は、以下の通りである。 The present invention has been made based on such knowledge, and the gist thereof is as follows.
第一の発明は、質量％で、Ｃ：０．０２％以下、Ｓｉ：０．７０％以下、Ｍｎ：０．５０％以下、Ｐ：０．０４％以下、Ｓ：０．０１％以下、Ａｌ：０．０１〜０．１５％、Ｎ：０．０２％以下、Ｃｒ：１６〜２３％、Ｎｉ：０．５０％以下、Ｔｉ：０．１０％以下、Ｎｂ：０．０１％以下、Ｚｒ：０．２０〜０．８０％、を含有し、残部Ｆｅおよび不可避的不純物からなり、仕上焼鈍後のフェライト粒の平均結晶粒径が１５μｍ以下であることを特徴とする耐リジング特性に優れたフェライト系ステンレス鋼板である。 1st invention is the mass%, C: 0.02% or less, Si: 0.70% or less, Mn: 0.50% or less, P: 0.04% or less, S: 0.01% or less, Al: 0.01 to 0.15%, N: 0.02% or less, Cr: 16 to 23%, Ni: 0.50% or less, Ti: 0.10% or less, Nb: 0.01% or less, Zr: 0.20 to 0.80%, comprising the balance Fe and inevitable impurities, and having excellent ridging resistance, characterized in that the average grain size of ferrite grains after finish annealing is 15 μm or less Ferritic stainless steel sheet.
第二の発明は、さらに、質量％で、Ｃｕ：０．３０〜０．８０％、Ｍｏ：０．１〜２．５％の中から選ばれる１種または２種を含有することを特徴とする第一の発明に記載の耐リジング特性に優れたフェライト系ステンレス鋼板である。 The second invention is characterized by further containing one or two kinds selected from Cu: 0.30 to 0.80% and Mo: 0.1 to 2.5% by mass%. This is a ferritic stainless steel sheet having excellent ridging resistance as described in the first invention.
第三の発明は、質量％で、Ｃ：０．０２％以下、Ｓｉ：０．７０％以下、Ｍｎ：０．５０％以下、Ｐ：０．０４％以下、Ｓ：０．０１％以下、Ａｌ：０．０１〜０．１５％、Ｎ：０．０２％以下、Ｃｒ：１６〜２３％、Ｎｉ：０．５０％以下、Ｔｉ：０．１０％以下、Ｎｂ：０．０１％以下、Ｚｒ：０．２０〜０．８０％、を含有し、残部Ｆｅおよび不可避的不純物からなる鋼素材を熱間圧延して熱延鋼板とし、該熱延鋼板を９００〜１０００℃の温度範囲で焼鈍し、次いで、酸洗、冷間圧延した後に８８０〜９６０℃の温度範囲で仕上焼鈍してフェライト粒の平均結晶粒径を１５μｍ以下とすることを特徴とする耐リジング特性に優れたフェライト系ステンレス鋼板の製造方法である。
The third invention is mass%, C: 0.02% or less, Si: 0.70% or less, Mn: 0.50% or less, P: 0.04% or less, S: 0.01% or less, Al: 0.01 to 0.15%, N: 0.02% or less, Cr: 16 to 23%, Ni: 0.50% or less, Ti: 0.10% or less, Nb: 0.01% or less, Zr: 0.20 to 0.80%, a steel material consisting of the balance Fe and inevitable impurities is hot-rolled into a hot-rolled steel sheet, and the hot-rolled steel sheet is annealed at a temperature range of 900 to 1000 ° C. Next, ferritic stainless steel having excellent ridging resistance, characterized in that after pickling and cold rolling, finish annealing is performed in a temperature range of 880 to 960 ° C. to make the average grain size of
第四の発明は、前記鋼素材の製鋼段階で、Ｚｒ源としてフェロジルコニウムを溶鋼中に添加することを特徴とする耐ジリング特性に優れたフェライト系ステンレス鋼板の製造方法である。 4th invention is a manufacturing method of the ferritic stainless steel plate excellent in the galling-proof characteristic characterized by adding ferrozirconium as a Zr source in molten steel in the steelmaking stage of the said steel raw material.
第五の発明は、前記鋼素材が、さらに、質量％で、Ｃｕ：０．３０〜０．８０％、Ｍｏ：０．１〜２．５％の中から選ばれる１種または２種を含有することを特徴とする第三の発明または第四の発明に記載の耐リジング特性に優れたフェライト系ステンレス鋼板の製造方法である。 According to a fifth aspect of the present invention, the steel material further includes one or two kinds selected from Cu: 0.30 to 0.80% and Mo: 0.1 to 2.5% by mass%. A method for producing a ferritic stainless steel sheet having excellent ridging resistance as described in the third or fourth invention.
本発明により、高額な鋳造設備の導入や生産性の低下を伴わずに、耐リジング特性に優れたフェライト系ステンレス鋼板を製造できる。また、本発明のフェライト系ステンレス鋼板は、耐食性にも極めて優れていることから、建材、建具、電機、産業機械、自動車、厨房用品、貯水器などの分野にも適用可能である。 According to the present invention, a ferritic stainless steel sheet having excellent ridging resistance can be manufactured without introducing expensive casting equipment and reducing productivity. Moreover, since the ferritic stainless steel sheet of the present invention is extremely excellent in corrosion resistance, it can also be applied to fields such as building materials, joinery, electric machinery, industrial machinery, automobiles, kitchen supplies, and water reservoirs.
以下、本発明を詳細に説明する。 Hereinafter, the present invention will be described in detail.
まず、本発明で最も重要となる仕上焼鈍板のフェライト粒の平均結晶粒径とＺｒ量について説明する。 First, the average grain size and Zr amount of ferrite grains of the finish annealed plate, which are the most important in the present invention, will be described.
リジング現象は、仕上焼鈍板の各フェライト粒の結晶方位による塑性変形能の差によって生じる鋼板表面の凹凸と考えられる。そこで、仕上焼鈍板のフェライト粒を微細化することが、塑性変形時の鋼板表面の凹凸の低減に寄与するものと考え、Ｃ、Ｎ安定化元素としてＺｒを含有させることに着目した。 The ridging phenomenon is considered to be unevenness on the surface of the steel sheet caused by the difference in plastic deformability depending on the crystal orientation of each ferrite grain of the finish annealed sheet. Therefore, it was considered that refinement of ferrite grains in the finish-annealed plate contributes to the reduction of irregularities on the surface of the steel plate during plastic deformation, and attention was paid to the inclusion of Zr as a C and N stabilizing element.
Ｚｒは、Ｎとの結合力がＴｉよりも強く、粗大なＴｉＮの生成を抑えるために有効に働く。また、ＣｒやＮを無害化して溶接部で粒界腐食が生じるのを防ぐ効果もある。さらに、微細なＺｒＮを生成するため、熱延板焼鈍後の組織を微細化し、冷延板焼鈍においても、フェライト粒の粒成長の進行を抑制する。 Zr has a stronger bonding force with N than Ti and works effectively to suppress the formation of coarse TiN. In addition, Cr and N are made harmless, and there is an effect of preventing the occurrence of intergranular corrosion at the weld. Furthermore, in order to produce | generate fine ZrN, the structure | tissue after hot-rolled sheet annealing is refined | miniaturized and progress of the grain growth of a ferrite grain is suppressed also in cold-rolled sheet annealing.
このような仕上焼鈍後の微細化への寄与以外に、Ｃ、Ｎ安定化元素としてＮｂを含有した場合のような再結晶温度の上昇もほとんどないため、普通鋼兼用設備である高速冷延板焼鈍ライン（タンデムーＣＡＬ）での製造が可能であり、生産性の面からも有利である。 In addition to contributing to refinement after such finish annealing, there is almost no increase in the recrystallization temperature as in the case of containing Nb as a C and N stabilizing element. Manufacture on an annealing line (tandemu CAL) is possible, which is advantageous from the standpoint of productivity.
そこで、表1に示すＺｒ量を変化させた組成を有する鋼を溶製し、スラブとした。該スラブを１１７０℃まで加熱し、６パスの粗圧延と６パスの仕上圧延により、仕上圧延温度を８５０℃、巻取温度を４５０℃とする熱間圧延を行って、板厚４．０ｍｍの熱延板とした。次に、この熱延板を９５０℃で６０秒の熱延板焼鈍を施した後、酸洗し、冷間圧延を行って、板厚０．８ｍｍの冷延板とした。更に、９００℃で６０秒の仕上焼鈍を施した。得られた仕上焼鈍板のフェライト粒の平均結晶粒径とリジング高さを、以下の方法により測定した。 Therefore, steel having a composition in which the amount of Zr shown in Table 1 was changed was melted to obtain a slab. The slab was heated to 1170 ° C., and hot rolling was performed at a finishing rolling temperature of 850 ° C. and a winding temperature of 450 ° C. by 6 passes of rough rolling and 6 passes of finish rolling, and the plate thickness was 4.0 mm. A hot-rolled sheet was used. Next, this hot-rolled sheet was subjected to hot-rolled sheet annealing at 950 ° C. for 60 seconds, followed by pickling and cold rolling to obtain a cold-rolled sheet having a thickness of 0.8 mm. Further, finish annealing was performed at 900 ° C. for 60 seconds. The average grain size and ridging height of the ferrite grains of the finished annealed plate were measured by the following method.
仕上焼鈍板のフェライト粒の平均結晶粒径について
平均結晶粒径は、得られた仕上焼鈍板の圧延方向（Ｌ方向）の断面において、板厚１/２位置、１/４位置および１/６位置のフェライト結晶粒度をＪＩＳ Ｇ０５５２(切断法)に準拠して求めた。
About average crystal grain size of ferrite grains of finish annealed plate The average crystal grain size is the thickness 1/2 position, 1/4 position and 1/6 in the cross section in the rolling direction (L direction) of the obtained finish annealed sheet. The ferrite crystal grain size at the position was determined according to JIS G0552 (cutting method).
フェライト結晶粒度から結晶粒径への換算は、前記ＪＩＳ Ｇ０５５２に準じて求めた。断面積１ｍｍ２当たりの結晶粒の数ｎをもとに、結晶粒を円近似し、
ｎ×ｒ２×π＝１ｍｍ２ から、結晶粒半径ｒを求め、結晶粒径（２ｒ）を算出した。
例えば、粒度番号６．０の場合、ｎ＝５１２個、結晶粒径の平均断面積は０．００１９５ｍｍ２となり、平均結晶粒径は４９．８μｍが得られる。
Conversion from the ferrite crystal grain size to the crystal grain size was determined according to JIS G0552. Based on the number n of crystal grains per 1 mm 2 in cross-sectional area, the crystal grains are circularly approximated,
The crystal grain radius r was determined from n × r 2 × π = 1 mm 2 and the crystal grain size (2r) was calculated.
For example, when the particle size number is 6.0, n = 512, the average cross-sectional area of the crystal grain size is 0.00195 mm 2 , and the average crystal grain size is 49.8 μm.
リジング高さについて
圧延方向と平行にＪＩＳ５号引張試験片を採取し、その表面を６００番のエメリー紙を用いて研磨した後、２０％の引張歪みを付与し、表面粗度計でリジング高さを測定した。ＪＩＳ Ｂ０６０１：２００１で規定される算術平均うねりＷａをリジング高さとした。
Ｗａの測定では、測定長１６ｍｍ、ハイカットフィルターの波長を０．８ｍｍ、ローカットフィルターの波長を２５ｍｍとした。
About ridging height After collecting JIS No. 5 tensile test piece in parallel with the rolling direction and polishing the surface with No. 600 emery paper, 20% tensile strain was applied, and ridging height was measured with a surface roughness meter. Was measured. The arithmetic mean waviness Wa defined in JIS B0601: 2001 was defined as the ridging height.
In the measurement of Wa, the measurement length was 16 mm, the wavelength of the high cut filter was 0.8 mm, and the wavelength of the low cut filter was 25 mm.
表１および図１に仕上焼鈍板のフェライト粒の平均結晶粒径およびリジング高さを示す。リジング高さが１０μｍ以下を耐リジング特性が良好の判定基準とした。図１から仕上焼鈍板のフェライト粒の平均結晶粒径が１５μｍ以下であれば、リジング高さが１０μｍ以下となり、優れた耐リジング特性が得られることがわかる。したがって、仕上焼鈍板のフェライト粒の平均結晶粒径は１５μｍ以下とする。 Table 1 and FIG. 1 show the average grain size and ridging height of the ferrite grains of the finish annealed plate. A ridging height of 10 μm or less was determined as a criterion for good ridging resistance. As can be seen from FIG. 1, when the average grain size of the ferrite grains of the finish annealed plate is 15 μm or less, the ridging height is 10 μm or less, and excellent ridging resistance is obtained. Accordingly, the average grain size of ferrite grains in the finish annealed plate is set to 15 μm or less.
Ｚｒ：０．２０〜０．８０質量％
次に、仕上焼鈍板のフェライト粒の平均結晶粒径が１５μｍ以下となるためのＺｒ含有量と適正な仕上焼鈍温度範囲を調べるため、表１の鋼Ｎｏ．２、３、５の冷延板を用いて、仕上焼鈍温度を８８０℃、９３０℃、９６０℃、１０００℃で６０秒焼鈍した仕上焼鈍板を作製し、フェライト粒の平均結晶粒径を評価した。その結果を表２に示す。
Zr: 0.20 to 0.80 mass%
Next, in order to investigate the Zr content and the appropriate finish annealing temperature range for the average grain size of the ferrite grains of the finish annealed plate to be 15 μm or less, the steel Nos. Using 2, 3, and 5 cold-rolled plates, finish annealing plates were annealed at 880 ° C., 930 ° C., 960 ° C., and 1000 ° C. for 60 seconds, and the average grain size of ferrite grains was evaluated. . The results are shown in Table 2.
表２の結果から、Ｚｒ量が０．１６質量％の仕上焼鈍板（２Ａ〜２Ｄ）では、仕上焼鈍温度を８８０℃まで低温化しても平均結晶粒径が１５μｍを超えていた。一方、Ｚｒ量が０．２１質量％の仕上焼鈍板（３Ａ〜３Ｄ）では、９６０℃以下の温度で仕上焼鈍を施した板Ｎｏ．３Ａ、３Ｂ、３Ｃの平均結晶粒径は１５μｍ以下と微細化した。更に、Ｚｒ量が０．４７質量％の仕上焼鈍板（５Ａ〜５Ｄ）では、仕上焼鈍温度を１０００℃まで高温化しても平均結晶粒径は１５μｍ以下の値が得られた。 From the results of Table 2, in the finish annealed plates (2A to 2D) having a Zr content of 0.16% by mass, the average crystal grain size exceeded 15 μm even when the finish annealing temperature was lowered to 880 ° C. On the other hand, in the finish annealed plates (3A to 3D) having a Zr amount of 0.21% by mass, the plate No. 1 subjected to finish annealing at a temperature of 960 ° C. or less. The average crystal grain size of 3A, 3B, and 3C was refined to 15 μm or less. Further, in the finish annealing plate (5A to 5D) having a Zr amount of 0.47% by mass, the average grain size was 15 μm or less even when the finish annealing temperature was increased to 1000 ° C.
このことから、仕上焼鈍板のフェライト粒を微細化するのに必要なＺｒ量は０．２０質量％以上とする。また、０．８０質量％を超えた含有は原料コストの高騰を招くため、Ｚｒ量は、０．２０〜０．８０質量％の範囲とする。 For this reason, the amount of Zr necessary to refine the ferrite grains of the finish-annealed plate is 0.20% by mass or more. Moreover, since inclusion exceeding 0.80 mass% causes the raw material cost to rise, the amount of Zr shall be 0.20-0.80 mass%.
なお、Ｚｒを溶鋼に含有させる際には、原料としてフェロジルコニウムを用いる。Ｚｒは、酸素との親和力が強く、溶鋼の脱酸が不十分な状態で原料を投入したり、スラグ上からフェロジルコニウムを投入するなどすると、その多くが酸化物となってしまい、仕上焼鈍板の結晶粒微細化のために本発明で重要となるＺｒＮの生成の役割を果たさなくなってしまう。このため、フェロジルコニウムの添加にあたっては、例えば、耐火物や鉄で作った筒状のワイヤや鉄製の箱の中にフェロジルコニウムを充填して、溶鋼へ直接投入するなどして、スラグ中の酸素とＺｒの反応を抑えるよう工夫することが大切である。 When Zr is contained in the molten steel, ferrozirconium is used as a raw material. Zr has a strong affinity with oxygen, and when raw materials are introduced in a state where the deoxidation of molten steel is insufficient, or when ferrozirconium is introduced from the slag, many of them become oxides, and the finish annealing plate Thus, the role of ZrN generation, which is important in the present invention for the refinement of crystal grains, is no longer fulfilled. For this reason, when adding ferrozirconium, for example, ferrozirconium is filled into a cylindrical wire or iron box made of refractory or iron and directly put into the molten steel. It is important to devise to suppress the reaction between Zr and Zr.
仕上焼鈍温度：８８０〜９６０℃
仕上焼鈍温度は低温のほうが仕上焼鈍後のフェライト粒が小さくなるが、８８０℃未満では再結晶が不十分となり、加工性が劣化するため、８８０℃以上とする。また、９６０℃を超えて仕上焼鈍した場合、含有するＺｒ量によって、仕上焼鈍板のフェライト粒の平均結晶粒径が１５μｍを超える場合があるので、仕上焼鈍温度の温度範囲は８８０〜９６０℃とする。好ましくは、８８０〜９２０℃の範囲である。
Finish annealing temperature: 880-960 ° C
The final annealing temperature is set to 880 ° C. or higher because the ferrite grain after the final annealing becomes smaller at a lower temperature, but recrystallization becomes insufficient at a temperature lower than 880 ° C. and the workability deteriorates. In addition, when the finish annealing is over 960 ° C., the average crystal grain size of the ferrite grains of the finish annealing plate may exceed 15 μm depending on the amount of Zr contained, so the temperature range of the finish annealing temperature is 880 to 960 ° C. To do. Preferably, it is the range of 880-920 degreeC.
以下にその他の成分組成及び製造条件について説明する。 Other component compositions and production conditions will be described below.
なお、以下の成分組成における％は全て質量％とする。 In addition,% in the following component composition shall be mass%.
Ｃ:０．０２％以下
Ｃは、強度を高める元素であるが、その量が０．０２％を超えると、延性が低下して加工性が劣化する。したがって、Ｃ量は０．０２％以下とする。
C: 0.02% or less C is an element that increases the strength. However, if its amount exceeds 0.02%, ductility decreases and workability deteriorates. Therefore, the C content is 0.02% or less.
Ｓｉ：０．７０％以下
Ｓｉは、脱酸剤として用いられる元素である。しかし、多量に含有すると硬質化して延性が低下する。したがって、Ｓｉ量は０．７０％以下とする。好ましくは、０．３０％以下である。
Si: 0.70% or less Si is an element used as a deoxidizer. However, when it contains abundantly, it will harden and ductility will fall. Therefore, the Si content is 0.70% or less. Preferably, it is 0.30% or less.
Ｍｎ：０．５０％以下
Ｍｎは、鋼の溶製段階で脱酸剤として用いられるが、その量が０．５０％を超えると、硫化物として析出し、耐食性を著しく低下させる。従って、Ｍｎ量は０．５０％以下とする。好ましくは、０．３０％以下である。
Mn: 0.50% or less Mn is used as a deoxidizer in the melting stage of steel, but if its amount exceeds 0.50%, it precipitates as a sulfide and significantly reduces the corrosion resistance. Therefore, the amount of Mn is 0.50% or less. Preferably, it is 0.30% or less.
Ｐ：０．０４％以下
Ｐが０．０４％を超えると、フェライト粒界へ偏析し、脆性破壊を誘起するとともに、硬質化させ、延性を低下させる。したがって、Ｐ量は０．０４％以下とする。
P: 0.04% or less When P exceeds 0.04%, it segregates to ferrite grain boundaries, induces brittle fracture, hardens, and decreases ductility. Therefore, the P content is 0.04% or less.
Ｓ：０．０１％以下
Ｓは、熱間加工性および耐食性の点から少ないほうが好ましい。したがって、Ｓ量は０．０１％以下とする。好ましくは、０．００５％以下である。
S: 0.01% or less S is preferably smaller in terms of hot workability and corrosion resistance. Therefore, the S content is 0.01% or less. Preferably, it is 0.005% or less.
Ａｌ：０．０１〜０．１５％
Ａｌは、溶製段階で鋼の脱酸剤として用いられるが、その効果を得るには０．０１％以上必要である。一方、過剰に含有すると粗大なＡｌ系介在物が生成して、表面疵の原因となるとともに、加工性を劣化させる。したがって、Ａｌ量は０．０１〜０．１５％の範囲とする。
Al: 0.01 to 0.15%
Al is used as a deoxidizer for steel in the melting stage, but 0.01% or more is necessary to obtain the effect. On the other hand, if contained excessively, coarse Al-based inclusions are generated, causing surface flaws and degrading workability. Therefore, the Al content is in the range of 0.01 to 0.15%.
Ｎ：０．０２％以下
Ｎが０．０２％を超えると、Ｃｒ窒化物として析出し、硬質化して延性が低下する。したがって、Ｎ量は０．０２％以下とする。
N: 0.02% or less When N exceeds 0.02%, it precipitates as Cr nitride, hardens, and ductility decreases. Therefore, the N content is 0.02% or less.
Ｃｒ：１６〜２３％
Ｃｒは、鋼板表面に不動態皮膜を形成して耐食性を高める元素である。こうした効果を得るには、Ｃｒ量を１６％以上とする必要がある。一方、Ｃｒ量が２３％を超えると靭性が低下するほか、強度上昇のため成形性が低下する。したがって、Ｃｒ量は１６〜２３％の範囲とする。
Cr: 16-23%
Cr is an element that improves the corrosion resistance by forming a passive film on the steel sheet surface. In order to obtain such an effect, the Cr content needs to be 16% or more. On the other hand, if the Cr content exceeds 23%, the toughness decreases and the formability decreases due to the increase in strength. Therefore, the Cr content is in the range of 16-23%.
Ｎｉ：０．５０％以下
Ｎｉは、隙間腐食を抑制させる効果を有する元素である。しかし、高価であることに加え、その量が０．５０％を超えると、硬質化させ、延性を低下させる。したがって、Ｎｉ量は０．５０％以下とする。
Ni: 0.50% or less Ni is an element having an effect of suppressing crevice corrosion. However, in addition to being expensive, when the amount exceeds 0.50%, it hardens and decreases ductility. Therefore, the Ni content is 0.50% or less.
Ｔｉ：０．１０％以下
Ｔｉは、溶接部の加工性や耐食性に有害なＣやＮをＴｉＣやＴｉＮとして無害化して加工性、耐食性を向上させる効果を持つ一方で、粗大なＴｉＮを生成するため、熱延焼鈍板、および仕上焼鈍板のフェライト粒の粗大化を誘起する。仕上焼鈍板のフェライト粒が粗大化した場合は、耐リジング特性が劣化する。したがって、Ｔｉ量は０．１０％以下とする。
Ti: 0.10% or less Ti has the effect of detoxifying C and N, which are harmful to the workability and corrosion resistance of welds, as TiC and TiN to improve workability and corrosion resistance, while generating coarse TiN Therefore, the ferrite grains of the hot-rolled annealed plate and the finish annealed plate are coarsened. When the ferrite grains of the finish annealed plate are coarsened, the ridging resistance is deteriorated. Therefore, the Ti amount is 0.10% or less.
Ｎｂ：０．０１％以下
Ｎｂは、微細なＮｂＣを生成し、フェライト結晶粒の微細化には有効であるが、０．０１％を超えると再結晶温度を上昇させるため、普通鋼を焼鈍するための高速冷延板焼鈍ラインでは焼鈍が不十分となり、仕上焼鈍板の加工性が低下する。したがって、Ｎｂ量は０．０１％以下とする。好ましくは、０．００５％以下である。
Nb: 0.01% or less Nb produces fine NbC and is effective for refining ferrite crystal grains. However, if it exceeds 0.01%, the recrystallization temperature is raised, so normal steel is annealed. Therefore, in the high-speed cold-rolled sheet annealing line, annealing becomes insufficient, and the workability of the finish-annealed sheet decreases. Therefore, the Nb content is 0.01% or less. Preferably, it is 0.005% or less.
本発明の基本成分元素は以上であるが、更に所望の特性を向上させる場合は、Ｃｕ、Ｍｏの１種または２種を選択元素として含有することができる。 Although the basic component elements of the present invention are as described above, in order to further improve desired characteristics, one or two of Cu and Mo can be contained as selective elements.
Ｃｕ：０．３０〜０．８０％
Ｃｕは、耐食性を向上させる重要な元素であり、特に隙間腐食を低減させるために必要な元素である。この効果を得るには０．３０％以上の含有が必要である。一方、０．８０％を超えて含有すると、熱間加工性が劣化するため、Ｃｕを含有する場合は、その量は０．３０〜０．８０％の範囲とすることが好ましい。更に好ましい範囲は０．３０〜０．５０％である。
ただし、特に高い耐食性を必要としない場合には、Ｃｕを含有しなくても良い。
Cu: 0.30 to 0.80%
Cu is an important element for improving the corrosion resistance, and is an element necessary particularly for reducing crevice corrosion. In order to obtain this effect, a content of 0.30% or more is necessary. On the other hand, if the content exceeds 0.80%, the hot workability deteriorates. Therefore, when Cu is contained, the amount is preferably in the range of 0.30 to 0.80%. A more preferable range is 0.30 to 0.50%.
However, Cu is not necessarily contained when high corrosion resistance is not required.
Ｍｏ：０．１〜２．５％
Ｍｏは、耐食性を向上させる元素であり、高い耐食性を必要とする場合には含有することが有効である。一方で、高価な元素であることに加えて、２．５％を超えて含有すると熱延板の靭性を低下させて製造性を低下させる懸念がある。さらに、仕上焼鈍板を硬質化させて、加工性を劣化させるので、Ｍｏを含有する場合は、その量は０．１〜２．５％の範囲とすることが好ましい。
Mo: 0.1-2.5%
Mo is an element that improves the corrosion resistance, and it is effective to contain it when high corrosion resistance is required. On the other hand, in addition to being an expensive element, when the content exceeds 2.5%, there is a concern that the toughness of the hot-rolled sheet is lowered and the productivity is lowered. Furthermore, since a finish annealing board is hardened and workability is deteriorated, when it contains Mo, it is preferable to make the quantity into the range of 0.1-2.5%.
なお、残部は、Ｆｅおよび不可避的不純物である。ただし、Ｖ、Ｃａ、Ｍｇ、Ｂは、不可避的不純物として許容される範囲で含有してもよい。その範囲は、Ｖ≦０．３％、Ｃａ≦０．００３％、Ｍｇ≦０．００３％、Ｂ≦０．００３％である。 The balance is Fe and inevitable impurities. However, V, Ca, Mg, and B may be contained within a range allowed as an inevitable impurity. The ranges are V ≦ 0.3%, Ca ≦ 0.003%, Mg ≦ 0.003%, and B ≦ 0.003%.
熱延板焼鈍温度：９００〜１０００℃
仕上焼鈍後のフェライト粒の結晶方位を分散させるには、熱延板焼鈍で十分に熱延組織を再結晶させる必要があるので、熱延板焼鈍温度は９００℃以上とする。一方、熱延板焼鈍温度が１０００℃を超えると結晶粒が粗大化した場合、仕上焼鈍後の結晶粒も大きくなるため、熱延板焼鈍温度は、９００〜１０００℃の温度範囲とする。好ましくは９２０〜９８０℃の範囲である。
Hot-rolled sheet annealing temperature: 900-1000 ° C
In order to disperse the crystal orientation of the ferrite grains after finish annealing, it is necessary to sufficiently recrystallize the hot-rolled structure by hot-rolled sheet annealing, so the hot-rolled sheet annealing temperature is set to 900 ° C. or higher. On the other hand, when the hot rolled sheet annealing temperature exceeds 1000 ° C., when the crystal grains become coarse, the crystal grains after finish annealing also increase, so the hot rolled sheet annealing temperature is set to a temperature range of 900 to 1000 ° C. Preferably it is the range of 920-980 degreeC.
前掲した表３に示す化学成分のフェライト系ステンレス鋼を溶製し、スラブとした後、１１７０℃に加熱して６パスの粗圧延と６パスの仕上圧延を行って、仕上温度を８５０℃、巻取温度を４５０℃として、板厚４．０ｍｍの熱延板とした。 After melting the ferritic stainless steel having the chemical composition shown in Table 3 and making it into a slab, it was heated to 1170 ° C. and subjected to 6-pass rough rolling and 6-pass finish rolling to a finishing temperature of 850 ° C., The coiling temperature was 450 ° C., and a hot-rolled sheet having a thickness of 4.0 mm was obtained.
ついで、表４に示す焼鈍温度で６０秒の熱延板焼鈍を行い、冷間圧延を行って、板厚０．８ｍｍの冷延板とした。さらに、表４に示す焼鈍温度で６０秒の仕上焼鈍を施して、得られた仕上焼鈍板のフェライト粒の平均結晶粒径とリジング高さを上述した方法で評価した結果を表４に併記する。 Subsequently, hot-rolled sheet annealing was performed for 60 seconds at the annealing temperature shown in Table 4, and cold rolling was performed to obtain a cold-rolled sheet having a thickness of 0.8 mm. Further, Table 4 shows the results of evaluating the average grain size and ridging height of the ferrite grains of the finished annealed plate obtained by performing the finish annealing for 60 seconds at the annealing temperature shown in Table 4 by the method described above. .
仕上焼鈍板のフェライト粒の平均結晶粒径が１５μｍを超えて、本発明範囲外である鋼Ｎｏ．１、２、３、８、１１、１２は、リジング高さが１０μｍ以上と耐リジング特性が悪い。これに対して、仕上焼鈍板のフェライト粒の平均結晶粒径が１５μｍ以下で本発明範囲である鋼Ｎｏ．４、５、６、７、９、１０、１３、１４、１５は、リジング高さが１０μｍ以下と良好な耐リジング特性を有している。 Steel No. 1 in which the average grain size of ferrite grains of the finish annealed plate exceeds 15 μm and is outside the scope of the present invention. 1, 2, 3, 8, 11, and 12 have a ridging resistance of 10 μm or more and poor ridging resistance. On the other hand, the average grain size of the ferrite grains of the finish annealed plate is 15 μm or less, and steel No. 1 is within the scope of the present invention. 4, 5, 6, 7, 9, 10, 13, 14, and 15 have good ridging resistance with a ridging height of 10 μm or less.
本発明のフェライト系ステンレス鋼板は、耐食性および耐リジング特性に優れていることから、建材、建具、電機、産業機械、自動車、厨房用品、貯水器などの分野にも適用することができる。 Since the ferritic stainless steel sheet of the present invention is excellent in corrosion resistance and ridging resistance, it can be applied to fields such as building materials, joinery, electrical machinery, industrial machinery, automobiles, kitchen supplies, and water reservoirs.
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