JP5709845B2 - Ferritic stainless steel sheet with excellent surface gloss and weather resistance and method for producing the same - Google Patents
Ferritic stainless steel sheet with excellent surface gloss and weather resistance and method for producing the same Download PDFInfo
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- 229910001220 stainless steel Inorganic materials 0.000 title claims description 45
- 238000004519 manufacturing process Methods 0.000 title claims description 24
- 229910000831 Steel Inorganic materials 0.000 claims description 26
- 238000000137 annealing Methods 0.000 claims description 26
- 239000010959 steel Substances 0.000 claims description 26
- 238000005098 hot rolling Methods 0.000 claims description 17
- 238000005097 cold rolling Methods 0.000 claims description 15
- 239000010935 stainless steel Substances 0.000 claims description 9
- 238000004804 winding Methods 0.000 claims description 9
- 238000000605 extraction Methods 0.000 claims description 8
- 238000001953 recrystallisation Methods 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 3
- 230000000694 effects Effects 0.000 description 17
- 230000007423 decrease Effects 0.000 description 11
- 230000003647 oxidation Effects 0.000 description 9
- 238000007254 oxidation reaction Methods 0.000 description 9
- 238000007670 refining Methods 0.000 description 8
- 229910052719 titanium Inorganic materials 0.000 description 8
- 238000000034 method Methods 0.000 description 6
- 229910052758 niobium Inorganic materials 0.000 description 6
- 238000005554 pickling Methods 0.000 description 6
- 230000000087 stabilizing effect Effects 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 5
- 239000010960 cold rolled steel Substances 0.000 description 5
- 229910052757 nitrogen Inorganic materials 0.000 description 5
- 229910052698 phosphorus Inorganic materials 0.000 description 5
- 229910052804 chromium Inorganic materials 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 238000005868 electrolysis reaction Methods 0.000 description 4
- 238000007654 immersion Methods 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- 150000003839 salts Chemical class 0.000 description 4
- 229910052718 tin Inorganic materials 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- DXHPZXWIPWDXHJ-UHFFFAOYSA-N carbon monosulfide Chemical compound [S+]#[C-] DXHPZXWIPWDXHJ-UHFFFAOYSA-N 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 230000007935 neutral effect Effects 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 235000013619 trace mineral Nutrition 0.000 description 3
- 239000011573 trace mineral Substances 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- KRHYYFGTRYWZRS-UHFFFAOYSA-N Fluorane Chemical compound F KRHYYFGTRYWZRS-UHFFFAOYSA-N 0.000 description 2
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 159000000011 group IA salts Chemical class 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 229910017604 nitric acid Inorganic materials 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000007921 spray Substances 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 206010039509 Scab Diseases 0.000 description 1
- 150000001447 alkali salts Chemical class 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000035558 fertility Effects 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
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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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- C22C38/001—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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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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
- C22C38/02—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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
本発明は、表面光沢と耐銹性に優れた省合金型の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 an alloy-saving ferritic stainless steel sheet excellent in surface gloss and weather resistance and a method for producing the same.
フェライト系ステンレス鋼板は、家電製品、厨房機器など屋内環境で耐銹性および表面品位が要求される分野で多用されている。これらフェライト系ステンレス鋼板の例として、JIS規格にSUS430LX、SUS430J1Lが挙げられる。また、非特許文献1には、耐銹性に優れるSUS430LXおよびSUS430J1Lの代表例が記載されている。これらフェライト系ステンレスは、CやNを低減し、Cr:16〜20%、Nb:0.3〜0.6%、さらにTiや微量のCuおよびMoを複合添加して孔食や発銹による表面性状の劣化を防止している。 Ferritic stainless steel sheets are widely used in fields that require weather resistance and surface quality in indoor environments such as home appliances and kitchen equipment. Examples of these ferritic stainless steel plates include SUS430LX and SUS430J1L in JIS standards. Non-Patent Document 1 describes typical examples of SUS430LX and SUS430J1L, which have excellent weather resistance. These ferritic stainless steels reduce C and N, Cr: 16 to 20%, Nb: 0.3 to 0.6%, and further by adding Ti, trace amounts of Cu and Mo in combination to cause pitting and cracking Deterioration of surface properties is prevented.
古くから、上述したNbやTiなどを添加したフェライト系ステンレス鋼板は、JISG4305、G4307に規定されるNo.2D仕上げもしくはNo.2B仕上げ品において、他のフェライト系ステンレス鋼(SUS430)と比較して、表面光沢が劣る欠点がある。特許文献1には、Ti、Nb等を添加したフェライト系ステンレス鋼において焼鈍での酸化スケール生成量を制御した表面光沢に優れた冷延鋼帯の製造方法が開示されている。また、特許文献2には冷延鋼帯の脱スケール方法、中性塩電解−硝酸電解の工程を規定した光沢と耐食性に優れたステンレス冷延鋼帯の製造方法、特許文献3には冷間圧延のワークロールの粗さや潤滑条件を制御した高光沢ステンレス鋼帯の製造方法が開示されている。 For a long time, ferritic stainless steel sheets to which the above-described Nb, Ti, and the like are added are Nos. Defined in JIS G4305 and G4307. 2D finish or No. The 2B finished product has a defect that the surface gloss is inferior compared with other ferritic stainless steels (SUS430). Patent Document 1 discloses a method for producing a cold-rolled steel strip excellent in surface gloss by controlling the amount of oxide scale generated during annealing in ferritic stainless steel to which Ti, Nb, etc. are added. Patent Document 2 discloses a method for descaling a cold-rolled steel strip, a method for producing a stainless cold-rolled steel strip excellent in gloss and corrosion resistance that defines a neutral salt electrolysis-nitric acid electrolysis process, and Patent Document 3 describes a cold A method for producing a high-gloss stainless steel strip in which the roughness and lubrication conditions of a rolling work roll are controlled is disclosed.
上述したフェライト系ステンレス鋼板は、近年価格高騰の著しいNiを多量に含有するオ−ステナイト系ステンレス鋼板よりも経済性に優れている。しかしながら、ステンレス鋼の構成元素であるCrの価格変動や希少元素であるNbの高騰を背景として、SUS430LXならびにSUS430J1Lについても将来に渡って十分な経済性を備えているとは言い難い現状にある。 The above-mentioned ferritic stainless steel sheet is more economical than the austenitic stainless steel sheet containing a large amount of Ni, which has recently experienced a marked increase in price. However, it is difficult to say that SUS430LX and SUS430J1L have sufficient economic efficiency in the future against the backdrop of price fluctuations of Cr, which is a constituent element of stainless steel, and soaring Nb, which is a rare element.
上記課題を解決する手段として、微量元素を利用して耐食性を改善する方法が考えられる。特許文献4および特許文献5には、Pを積極的に添加して耐候性、耐銹性、耐隙間腐食性を改善するフェライト系ステンレス鋼が開示されている。特許文献4は、Cr:20%超〜40%、P:0.06%超〜0.2%以下とした高Cr、P添加フェライト系ステンレス鋼である。特許文献5は、Cr:11%〜20%未満、P:0.04%超〜0.2%以下としたP添加フェライト系ステンレス鋼である。しかしながら、Pは、製造性、加工性、溶接性を阻害する要因となる。 As a means for solving the above problems, a method of improving the corrosion resistance using a trace element can be considered. Patent Documents 4 and 5 disclose ferritic stainless steels that are positively added with P to improve weather resistance, weather resistance, and crevice corrosion resistance. Patent Document 4 is a high Cr, P-added ferritic stainless steel with Cr: more than 20% to 40% and P: more than 0.06% to 0.2% or less. Patent Document 5 is a P-added ferritic stainless steel having Cr: 11% to less than 20% and P: more than 0.04% to 0.2% or less. However, P is a factor that impedes manufacturability, workability, and weldability.
これまで本発明者らも、経済性の観点から、CrやMoの合金化によらず、微量元素を利用して耐銹性を改善したフェライト系ステンレス鋼について開示している。特許文献6は、Cr:13〜22%、Sn:0.001〜1%でC、N、Si、Mn、Pを低減し、安定化元素としてTiを0.08〜0.35%添加したフェライト系ステンレス鋼である。しかしながら、これら文献では、前述したような表面光沢への影響については何ら検討されていない。 So far, the present inventors have also disclosed a ferritic stainless steel having improved weather resistance using trace elements, regardless of alloying of Cr and Mo, from the viewpoint of economy. In Patent Document 6, Cr: 13 to 22%, Sn: 0.001 to 1%, C, N, Si, Mn, and P are reduced, and Ti is added as a stabilizing element 0.08 to 0.35%. Ferritic stainless steel. However, these documents do not discuss the influence on the surface gloss as described above.
上述した通り、16%以上のCrを含有しNb等の安定化元素を添加したSUS430LXならびにSUS430J1Lは、将来に渡っての経済性には課題がある。一方で、微量元素を利用して耐銹性を向上したフェライト系ステンレス鋼は、製造性や表面光沢の視点から課題がある。近年、家電製品、厨房機器などに使用されるステンレス鋼板は表面光沢の向上に対する要求が高まりつつある。
そこで本発明は、省合金型のフェライト系ステンレス鋼板において、Cr量16%未満でSUS430LXやSUS430J1Lと遜色ない耐銹性を有し、表面光沢を飛躍的に向上させることを課題とし、これを実現化した省合金型のフェライト系ステンレス鋼板とその製造方法を提供することを目的とする。As described above, SUS430LX and SUS430J1L containing 16% or more of Cr and added with a stabilizing element such as Nb have a problem in economical efficiency in the future. On the other hand, ferritic stainless steel with improved weather resistance using trace elements has problems from the viewpoint of manufacturability and surface gloss. In recent years, there is an increasing demand for improving the surface gloss of stainless steel plates used for home appliances, kitchen appliances, and the like.
Therefore, the present invention has an object to achieve a dramatic improvement in surface gloss in an alloy-saving ferritic stainless steel sheet that has a Cr content of less than 16% and is comparable to SUS430LX and SUS430J1L, and achieves this. An object of the present invention is to provide an alloy-saving ferritic stainless steel sheet and a method for producing the same.
本発明者らは、前記した課題を解決するために鋭意検討した結果、Cr量16%未満のフェライト系ステンレス鋼において、Sn添加による耐銹性向上効果に加えて、安定化元素であるNbやTiの添加と表面光沢の関係について以下の新しい知見を得て本発明を成すに至った。 As a result of intensive studies to solve the above-mentioned problems, the present inventors have found that in ferritic stainless steel with a Cr content of less than 16%, in addition to the effect of improving the weather resistance by adding Sn, The following new knowledge about the relationship between the addition of Ti and the surface gloss was obtained and the present invention was achieved.
(a)微量Sn添加による耐銹性向上効果を発現させるには12%以上のCr量が必要である。加えて、Crと微量Snからなる不働態皮膜の健全性を維持するにはC、N、Si、Mn、P、Sを低減して、NbやTiの安定化元素を添加することが効果的である。 (A) A Cr amount of 12% or more is required to exhibit the effect of improving weather resistance by adding a small amount of Sn. In addition, it is effective to reduce the C, N, Si, Mn, P, and S and to add a stabilizing element such as Nb or Ti to maintain the soundness of the passive film composed of Cr and a small amount of Sn. It is.
(b)Nbは、耐銹性に加えて表面光沢の向上作用を発現させる有効な安定化元素である。微量Sn添加鋼において、その作用は0.05%から発現する。但し、0.3%以上添加すると、鋼材の熱延加熱温度ならびに焼鈍温度の上昇により酸化スケールに起因する表面光沢の低下を招く。 (B) Nb is an effective stabilizing element that exhibits an effect of improving surface gloss in addition to weather resistance. In a small amount of Sn-added steel, the effect appears from 0.05%. However, when 0.3% or more is added, the surface gloss due to the oxide scale is lowered due to the increase in the hot rolling heating temperature and the annealing temperature of the steel material.
(c)Tiは、C、Nを固定する安定化元素としての作用に加えて、熱延加熱時にTi系炭硫化物(例えばTi4C2S2)を生成して、発銹起点となるMnSやCaSの生成を抑止する。微量Sn添加鋼において、その作用は0.03%から発現する。但し、0.15%以上添加すると、介在物起因のへげ疵や酸化皮膜中へのTi濃化により表面光沢の低下を招く。(C) In addition to the action as a stabilizing element that fixes C and N, Ti generates Ti-based carbon sulfide (for example, Ti 4 C 2 S 2 ) during hot rolling and becomes a starting point. Suppresses the generation of MnS and CaS. In a small amount of Sn-added steel, the action starts from 0.03%. However, if added in an amount of 0.15% or more, the surface gloss is lowered due to the haze caused by inclusions and the concentration of Ti in the oxide film.
(d)前記した微量Sn添加鋼におけるNbとTiの効果は、1≦Nb/Ti≦3.5の範囲で複合添加した場合に顕在化することを見出した。つまり、微量Sn添加鋼の耐銹性と表面光沢向上には、表面光沢の向上作用が大きいNbを主体に添加し、発銹起点を抑止して不働態皮膜の健全性を維持するために微量Tiとの複合添加とすることが効果的であることを知見した。 (D) It has been found that the effects of Nb and Ti in the above-described small amount of Sn-added steel are manifested when they are added together in the range of 1 ≦ Nb / Ti ≦ 3.5. In other words, in order to improve the weather resistance and surface gloss of a small amount of Sn-added steel, Nb, which has a large effect of improving the surface gloss, is mainly added to suppress the starting point and maintain the soundness of the passive film. It has been found that the combined addition with Ti is effective.
(e)Nb添加による表面光沢向上作用については未だ不明なところも多いものの、表面光沢の低下要因である熱延加熱や焼鈍時の内部酸化と粒界酸化は固溶Snに加えて、固溶Nbの存在により一層抑制される。従って、Nb添加による光沢向上効果は、固溶Snとの重畳により発現していると推察する。 (E) Although there are still many unclear points about the surface gloss improvement effect due to the addition of Nb, the internal oxidation and grain boundary oxidation during hot rolling and annealing, which are the causes of the reduction in surface gloss, are in addition to solid solution Sn. It is further suppressed by the presence of Nb. Therefore, it is speculated that the gloss improvement effect due to the addition of Nb is manifested by superposition with solute Sn.
(f)熱延加熱後の抽出温度は、表面光沢向上の視点から、へげ疵を誘発する鋳片表層の介在物を除去するためのスケール生成量を確保し、Ti系炭硫化物(例えばTi4C2S2)を生成して発銹起点となるMnSやCaSの生成を抑止する温度とする。Cr量16%未満の微量Sn添加鋼では1080〜1190℃とすることが効果的である。(F) The extraction temperature after hot-rolling heating ensures the amount of scale generation for removing inclusions on the slab surface layer that induces glazing from the viewpoint of improving surface gloss, and Ti-based carbon sulfide (for example, Ti 4 C 2 S 2 ) is generated, and the temperature is set to suppress the generation of MnS and CaS as starting points. In the case of a small amount of Sn-added steel with a Cr content of less than 16%, it is effective to set the temperature to 1800 to 1190 ° C.
(g)熱間圧延後の巻取りは、表面光沢向上の視点から、巻取り時の表面疵を抑制し、光沢低下を招く内部酸化物や粒界酸化を抑制する温度とする。Cr量16%未満の微量Sn添加鋼では500〜700℃とすることが効果的である。また、焼鈍温度は、光沢を担保する視点から980℃以下とすることが効果的である。 (G) From the viewpoint of improving surface gloss, the winding after hot rolling is performed at a temperature that suppresses surface wrinkling during winding and suppresses internal oxides and grain boundary oxidation that cause a decrease in gloss. In a small amount of Sn-added steel with a Cr content of less than 16%, it is effective to set the temperature to 500 to 700 ° C. Moreover, it is effective that the annealing temperature is 980 ° C. or less from the viewpoint of ensuring gloss.
上記(a)〜(g)の知見に基づいて成された本発明の要旨は、以下の通りである。 The gist of the present invention based on the findings (a) to (g) is as follows.
(1)質量%にて、
C:0.001〜0.03%、
Si:0.01〜1.0%、
Mn:0.01〜1.5%、
P:0.005〜0.05%、
S:0.0001〜0.01%、
Cr:12〜16%、
N:0.001〜0.03%、
Nb:0.05〜0.3%、
Ti:0.03〜0.15%、
Al:0.005〜0.5%、
Sn:0.01〜1.0%、
残部がFeおよび不可避的不純物からなり、
1≦Nb/Ti≦3.5の関係を満たすことを特徴とする表面光沢と耐銹性に優れたフェライト系ステンレス鋼板。(1) In mass%,
C: 0.001 to 0.03%,
Si: 0.01 to 1.0%,
Mn: 0.01 to 1.5%,
P: 0.005 to 0.05%,
S: 0.0001 to 0.01%,
Cr: 12-16%,
N: 0.001 to 0.03%,
Nb: 0.05-0.3%
Ti: 0.03-0.15%,
Al: 0.005 to 0.5%,
Sn: 0.01-1.0%,
The balance consists of Fe and inevitable impurities,
A ferritic stainless steel sheet excellent in surface gloss and weather resistance, characterized by satisfying a relationship of 1 ≦ Nb / Ti ≦ 3.5.
(2)前記ステンレス鋼板が、さらに質量%にて、
Ni:0.01〜0.5%、
Cu:0.01〜0.5%、
Mo:0.01〜0.5%、
V:0.01〜0.5%、
Zr:0.01〜0.5%、
Co:0.01〜0.5%、
Mg:0.0001〜0.005%、
B:0.0003〜0.005%、
Ca:0.0003〜0.005%
の1種または2種以上含有していることを特徴とする(1)に記載の表面光沢と耐銹性に優れたフェライト系ステンレス鋼板。(2) The stainless steel plate is further in mass%,
Ni: 0.01 to 0.5%,
Cu: 0.01 to 0.5%,
Mo: 0.01 to 0.5%,
V: 0.01-0.5%
Zr: 0.01 to 0.5%,
Co: 0.01 to 0.5%
Mg: 0.0001 to 0.005%,
B: 0.0003 to 0.005%,
Ca: 0.0003 to 0.005%
The ferritic stainless steel sheet having excellent surface gloss and weather resistance according to (1), characterized in that one or more of the above are contained.
(3)前記(1)または(2)に記載の鋼成分を有するステンレス鋼のスラブを加熱して、抽出温度1080〜1190℃で加熱炉から抽出後熱間圧延をし、巻取り温度を500〜700℃で巻き取ることを特徴とする表面光沢と耐銹性に優れたフェライト系ステンレス鋼板の製造方法。 (3) The stainless steel slab having the steel component described in the above (1) or (2) is heated, extracted from a heating furnace at an extraction temperature of 1,800 to 1,190 ° C., and then hot-rolled, and the coiling temperature is set to 500. A method for producing a ferritic stainless steel sheet excellent in surface gloss and weather resistance, characterized by winding at ~ 700 ° C.
(4)前記熱間圧延の巻取り後、冷間圧延を行い、その後、850〜980℃で仕上げ焼鈍を行うことを特徴とする(3)に記載の表面光沢と耐銹性に優れたフェライト系ステンレス鋼板の製造方法。 (4) Ferrite excellent in surface gloss and weather resistance according to (3), wherein after hot rolling is wound, cold rolling is performed, and then finish annealing is performed at 850 to 980 ° C. Of manufacturing stainless steel sheet.
(5)前記熱間圧延の巻取り後、中間焼鈍を挟む2回以上の冷間圧延を行い、その後、850〜980℃で仕上げ焼鈍を行うことを特徴とする(3)に記載の表面光沢と耐銹性に優れたフェライト系ステンレス鋼板の製造方法。 (5) The surface gloss according to (3), wherein after the hot rolling is wound, cold rolling is performed twice or more with intermediate annealing, followed by finish annealing at 850 to 980 ° C. And ferritic stainless steel sheet with excellent weather resistance.
(6)前記熱間圧延の巻取り後、冷間圧延の前に、熱延板焼鈍を再結晶温度以上1050℃以下の焼鈍温度で行うことを特徴とする(4)または(5)に記載の表面光沢と耐銹性に優れたフェライト系ステンレス鋼板の製造方法。 (6) The hot-rolled sheet annealing is performed at an annealing temperature of a recrystallization temperature or higher and 1050 ° C. or lower after the hot rolling and before cold rolling, as described in (4) or (5) Of ferritic stainless steel sheet with excellent surface gloss and weather resistance.
本発明によれば、合金コストや製造コストの上昇を招くことなく経済性に優れ、SUS430LXやSUS430J1Lと遜色ない耐銹性を有し、表面光沢を飛躍的に向上した、表面光沢と耐銹性に優れた省合金型のフェライト系ステンレス鋼板を得ることができるという顕著な効果を奏するものである。 According to the present invention, the surface gloss and the weather resistance are excellent, which is excellent in economic efficiency without causing an increase in alloy costs and manufacturing costs, has a weather resistance comparable to SUS430LX and SUS430J1L, and has dramatically improved the surface gloss. It is possible to obtain a remarkable effect that an alloy-saving ferritic stainless steel sheet having excellent resistance can be obtained.
以下、本発明の各要件について詳しく説明する。なお、各元素の含有量の「%」表示は「質量%」を意味する。 Hereinafter, each requirement of the present invention will be described in detail. In addition, "%" display of the content of each element means "mass%".
[I]成分の限定理由を以下に説明する。
Cは、耐銹性を劣化させるため、その含有量の上限を0.03%とする。耐銹性の観点からその含有量は少ないほど良く、その上限は、好ましくは0.02%、より好ましくは0.01%、さらに好ましくは0.005%とするとよい。また、過度の低減は精錬コストの増加に繋がるため、その含有量の下限を0.001%とする。耐銹性や製造コストを考慮すると、その下限は、好ましくは0.002%とするとよい。The reason for limiting the component [I] will be described below.
C degrades weather resistance, so the upper limit of its content is 0.03%. From the viewpoint of weather resistance, the lower the content, the better. The upper limit is preferably 0.02%, more preferably 0.01%, and even more preferably 0.005%. Moreover, since excessive reduction leads to the increase in refining cost, the minimum of the content shall be 0.001%. In consideration of weather resistance and production cost, the lower limit is preferably 0.002%.
Siは、脱酸元素として添加される場合がある。しかし、Siは、固溶強化元素であり、加工性の低下抑制から上限を1.0%とする。加工性の観点からその含有量は少ないほど良く、その上限を、好ましくは0.6%、より好ましくは0.3%、さらに好ましくは0.2%とするとよい。また、過度の低減は精錬コストの増加に繋がるため、Si含有量の下限を0.01%とする。加工性や製造コストを考慮すると、その下限を、好ましくは0.05%とするとよい。 Si may be added as a deoxidizing element. However, Si is a solid solution strengthening element, and the upper limit is set to 1.0% in order to suppress a decrease in workability. From the viewpoint of workability, the lower the content, the better. The upper limit is preferably 0.6%, more preferably 0.3%, and even more preferably 0.2%. Moreover, since excessive reduction leads to the increase in refining cost, the minimum of Si content shall be 0.01%. In consideration of workability and manufacturing cost, the lower limit is preferably 0.05%.
Mnは、発銹の起点となるMnSを生成し耐銹性を阻害する元素であるため、その含有量は少ないほど良い。耐銹性の低下抑制からその含有量の上限を1.5%とする。耐銹性の観点からその含有量は少ないほど良く、その上限は、好ましくは1.0%、より好ましくは0.3%、さらに好ましくは0.2%とするとよい。また、過度の低減は精錬コストの増加に繋がるため、Mnの含有量の下限を0.01%とする。好ましくは、耐銹性と製造コストを考慮すると、その下限を0.05%とするとよい。 Since Mn is an element that generates MnS as a starting point of wrinkling and inhibits weathering resistance, the smaller the content, the better. The upper limit of the content is set to 1.5% from the suppression of deterioration of weather resistance. From the viewpoint of weather resistance, the lower the content, the better. The upper limit is preferably 1.0%, more preferably 0.3%, and even more preferably 0.2%. Moreover, since excessive reduction leads to the increase in refining cost, the minimum of content of Mn shall be 0.01%. Preferably, considering weather resistance and manufacturing cost, the lower limit may be 0.05%.
Pは、製造性や溶接性を阻害する元素であるため、その含有量は少ないほど良い。製造性や溶接性の低下抑制からその含有量の上限を0.05%とする。製造性や溶接性の観点からその含有量は少ないほど良く、その上限は、好ましくは0.04%、より好ましくは0.03%とするとよい。また、過度の低減は精錬コストの増加に繋がるため、Pの含有量の下限を0.005%とする。より好ましくは、製造コストを考慮して0.01%とするとよい。 Since P is an element that impairs manufacturability and weldability, the smaller the content, the better. The upper limit of the content is set to 0.05% in order to suppress the decrease in manufacturability and weldability. From the viewpoint of manufacturability and weldability, the smaller the content, the better. The upper limit is preferably 0.04%, more preferably 0.03%. Moreover, since excessive reduction leads to the increase in refining cost, the lower limit of the P content is set to 0.005%. More preferably, it is good to set it as 0.01% in consideration of manufacturing cost.
Sは、不純物元素であり、耐銹性や熱間加工性を阻害するため、その含有量は少ないほど良い。耐銹性や熱間加工性を確保するため、Sの含有量の上限は0.01%とする。耐銹性や熱間加工性の観点からその含有量は少ないほど良く、その上限は、好ましくは0.005%、より好ましくは0.003%、さらに好ましくは0.002%とするとよい。また、過度の低減は精錬コストの増加に繋がるため、好ましくはその含有量の下限を0.0001%とする。より好ましくは、耐銹性や製造コストを考慮して0.0002%とするとよい。 S is an impurity element and hinders weather resistance and hot workability, so the smaller the content, the better. In order to ensure weather resistance and hot workability, the upper limit of the S content is 0.01%. The content is preferably as small as possible from the viewpoint of weather resistance and hot workability, and the upper limit is preferably 0.005%, more preferably 0.003%, and even more preferably 0.002%. Moreover, since excessive reduction leads to the increase in refining cost, Preferably the minimum of the content shall be 0.0001%. More preferably, the content is 0.0002% in consideration of weather resistance and manufacturing cost.
Crは、フェライト系ステンレス鋼の構成元素であり耐銹性を確保するための必須の元素である。本発明の耐銹性を確保するために下限は12%とする。上限は、SUS430LXと比較した経済性の観点から、16%とする。耐銹性とSn添加量を考慮して、好ましくは、13〜15%とする。 Cr is a constituent element of ferritic stainless steel and an essential element for ensuring weather resistance. In order to ensure the weather resistance of the present invention, the lower limit is 12%. The upper limit is 16% from the viewpoint of economy compared with SUS430LX. Considering weather resistance and Sn addition amount, it is preferably 13 to 15%.
Nは、Cと同様に耐銹性を劣化させるため、その含有量は少ないほど良いため、上限を0.03%とする。耐銹性の観点からその含有量は少ないほど良く、その上限は、好ましくは0.02%、より好ましくは0.012%とするとよい。また、過度の低減は精錬コストの増加に繋がるため、好ましくは下限を0.001%とする。より好ましくは、耐銹性や製造コストを考慮して0.005%とするとよい。 N, like C, deteriorates weather resistance, so the lower the content, the better. Therefore, the upper limit is made 0.03%. From the viewpoint of weather resistance, the lower the content, the better. The upper limit is preferably 0.02%, more preferably 0.012%. Moreover, since excessive reduction leads to the increase in refining cost, Preferably a minimum is made into 0.001%. More preferably, the content is 0.005% in consideration of weather resistance and manufacturing cost.
Nbは、本発明の微量Sn添加鋼において耐銹性の向上に加えて、表面光沢を向上させる必須の元素である。上記効果は0.05%以上から発現する。しかし、過度な添加は、鋼の再結晶温度を上昇させて、逆に表面光沢の低下をもたらす。従って、上限を0.3%とする。好ましくは、耐銹性と表面光沢および製造性を考慮して0.1〜0.2%とする。 Nb is an essential element for improving surface gloss in addition to improving weather resistance in the trace amount Sn-added steel of the present invention. The above effect is manifested from 0.05% or more. However, excessive addition raises the recrystallization temperature of the steel and conversely causes a reduction in surface gloss. Therefore, the upper limit is made 0.3%. Preferably, considering the weather resistance, surface gloss and manufacturability, the content is made 0.1 to 0.2%.
Tiは、C、Nを固定する安定化元素としての作用に加えて、耐銹性を向上させる必須の元素である。上記効果は、0.03%から発現する。しかし、過度な添加は、介在物起因のへげ疵や酸化皮膜中へのTi濃化により表面光沢の低下を招く。従って、上限を0.15%とする。好ましくは、耐銹性と表面光沢および製造性を考慮して0.05〜0.1%とする。 Ti is an essential element for improving weather resistance in addition to the action as a stabilizing element for fixing C and N. The above effect is manifested from 0.03%. However, excessive addition leads to a decrease in surface gloss due to the haze caused by inclusions and Ti concentration in the oxide film. Therefore, the upper limit is made 0.15%. Preferably, considering the weather resistance, surface gloss and manufacturability, the content is made 0.05 to 0.1%.
Alは、脱酸元素として有効な元素であるため、その含有量の下限を0.005%とした。しかし、過度の添加は加工性や靭性および溶接性の劣化をもたらすため、Alの含有量の上限を0.5%とした。加工性、靭性や溶接性の観点からその含有量は少ないほど良く、その上限は、好ましくは0.1%、より好ましくは0.05%、さらに好ましくは0.03%とするとよい。また、精錬コストを考慮して、その含有量の下限は、より好ましくは0.01%とするとよい。 Since Al is an element effective as a deoxidizing element, the lower limit of its content was set to 0.005%. However, excessive addition causes deterioration of workability, toughness and weldability, so the upper limit of the Al content is set to 0.5%. From the viewpoint of workability, toughness and weldability, the lower the content, the better. The upper limit is preferably 0.1%, more preferably 0.05%, and even more preferably 0.03%. In consideration of the refining cost, the lower limit of the content is more preferably 0.01%.
Snは、CrやMoの合金化ならびに希少元素であるNiやCo等の添加に頼ることなく、本発明の目標とする耐銹性を確保するために必須の元素である。本発明の目標とする耐銹性を得るために、Snの含有量の下限を0.01%とした。耐銹性をより確保するため、好ましくは、0.05%以上、より好ましくは0.1%以上とするとよい。しかし、過度の添加は、表面光沢や製造性の低下に繋がるとともに、耐銹性向上効果も飽和する。そのため、上限を1.0%とした。耐銹性や表面光沢を考慮すると、その含有量の上限を0.5%以下、より好ましくは、0.3%、さらに好ましくは、上限を0.2%とするとよい。 Sn is an indispensable element for ensuring the target weather resistance of the present invention without resorting to alloying of Cr and Mo and addition of rare elements such as Ni and Co. In order to obtain the target weather resistance of the present invention, the lower limit of the Sn content was set to 0.01%. In order to further ensure weather resistance, it is preferably 0.05% or more, more preferably 0.1% or more. However, excessive addition leads to a decrease in surface gloss and manufacturability, and the effect of improving weather resistance is saturated. Therefore, the upper limit was made 1.0%. In consideration of weather resistance and surface gloss, the upper limit of the content is 0.5% or less, more preferably 0.3%, and still more preferably 0.2%.
NbとTiは前記した範囲で添加し、かつその添加量は、本発明の目標とする耐銹性と表面光沢を得るために、1≦Nb/Ti≦3.5を満たすものとする。Nb/Ti<1の場合、Ti系介在物やTi系酸化物に起因する表面光沢の低下を招く。一方、3.5<Nb/Tiの場合、熱延加熱温度ならびに焼鈍温度の上昇による内部酸化や粒界酸化に起因する表面光沢の低下を招く。より好ましい範囲は、本発明の目標とする耐銹性と表面光沢を考慮して1.5≦Nb/Ti≦3とする。 Nb and Ti are added in the above-described ranges, and the addition amount satisfies 1 ≦ Nb / Ti ≦ 3.5 in order to obtain the target weather resistance and surface gloss of the present invention. In the case of Nb / Ti <1, the surface gloss due to Ti inclusions and Ti oxides is reduced. On the other hand, in the case of 3.5 <Nb / Ti, the surface gloss is reduced due to internal oxidation or grain boundary oxidation due to an increase in hot rolling heating temperature and annealing temperature. A more preferable range is 1.5 ≦ Nb / Ti ≦ 3 in consideration of the target weather resistance and surface gloss of the present invention.
Ni、Cu、Mo、V、Zr、Coは、Snとの相乗効果により耐銹性を向上させる元素であり、必要に応じて添加してもよい。添加する場合は、その効果が発現する0.01%以上、好ましくは0.02%以上とする。より好ましくは効果発現が顕著となる0.05%以上とする。但し、0.5%を超えると、材料コストの上昇や表面光沢の低下を招くため、各々の含有量の上限を0.5%とする。これら元素は希少であるため、添加する場合、Ni,Cuの好ましい範囲は0.1〜0.4%、Moの好ましい範囲は0.1〜0.3%である。V,Zr,Coの好ましい範囲は0.02〜0.3%である。 Ni, Cu, Mo, V, Zr, and Co are elements that improve weather resistance due to a synergistic effect with Sn, and may be added as necessary. When added, the effect is 0.01% or more, preferably 0.02% or more. More preferably, it is made 0.05% or more at which the effect expression becomes remarkable. However, if it exceeds 0.5%, the material cost increases and the surface gloss decreases, so the upper limit of each content is set to 0.5%. Since these elements are rare, when added, the preferable range of Ni and Cu is 0.1 to 0.4%, and the preferable range of Mo is 0.1 to 0.3%. A preferable range of V, Zr, and Co is 0.02 to 0.3%.
Mgは、溶鋼中でAlとともにMg酸化物を形成し脱酸剤として作用する他、TiNの晶出核として作用する。TiNは凝固過程においてフェライト相の凝固核となり、TiNの晶出を促進させることで、凝固時にフェライト相を微細生成させることができる。凝固組織を微細化させることにより、製品のリジングやロ−ピングなどの粗大凝固組織に起因した表面欠陥を防止できる他、加工性の向上をもたらすため必要に応じて添加してもよい。添加する場合は、これら効果を発現する0.0001%以上とする。但し、0.005%を超えると製造性が劣化するため、上限を0.005%とする。好ましくは、製造性を考慮して、その含有量を0.0003〜0.002%とする。 Mg forms Mg oxide with Al in molten steel and acts as a deoxidizer, and also acts as a crystallization nucleus of TiN. TiN becomes a solidification nucleus of the ferrite phase in the solidification process, and by facilitating crystallization of TiN, the ferrite phase can be finely formed during solidification. By refining the solidified structure, surface defects caused by coarse solidified structure such as ridging and roping of the product can be prevented, and it may be added as necessary to improve workability. When added, the content is made 0.0001% or more to express these effects. However, if it exceeds 0.005%, manufacturability deteriorates, so the upper limit is made 0.005%. Preferably, considering the manufacturability, the content is made 0.0003 to 0.002%.
Bは、熱間加工性や2次加工性を向上させる元素であり、フェライト系ステンレス鋼への添加は有効であるので、必要に応じて添加してもよい。添加する場合は、これら効果を発現する0.0003%以上とする。しかし、過度の添加は、伸びの低下をもたらすため、上限を0.005%とする。好ましくは、材料コストや加工性を考慮して、その含有量を0.0005〜0.002%とする。 B is an element that improves hot workability and secondary workability. Since addition to ferritic stainless steel is effective, B may be added as necessary. When adding, it is made 0.0003% or more to express these effects. However, excessive addition causes a decrease in elongation, so the upper limit is made 0.005%. Preferably, considering the material cost and workability, the content is made 0.0005 to 0.002%.
Caは、熱間加工性や鋼の清浄度を向上させる元素であり、必要に応じて添加してもよい。添加する場合は、これら効果を発現する0.0003%以上とする。しかし、過度の添加は、製造性の低下やCaSなどの水溶性介在物による耐食性の低下に繋がるため、上限を0.005%とする。好ましくは、製造性や耐銹性を考慮して、その含有量を0.0003〜0.0015%とする。 Ca is an element that improves hot workability and steel cleanliness, and may be added as necessary. When adding, it is made 0.0003% or more to express these effects. However, excessive addition leads to a decrease in manufacturability and a decrease in corrosion resistance due to water-soluble inclusions such as CaS, so the upper limit is made 0.005%. Preferably, considering the manufacturability and weather resistance, the content is made 0.0003 to 0.0015%.
[II]製造方法に関する限定理由を以下に説明する。
前記[I]項で示した成分を有し、SUS430LXやSUS430J1Lと遜色ない耐銹性ならびにそれを凌駕する表面光沢を得るために必要な製造方法の一例を示す。[II] The reason for limitation regarding the manufacturing method will be described below.
An example of a production method having the components shown in the above item [I] and necessary for obtaining a weather resistance comparable to that of SUS430LX or SUS430J1L and a surface gloss surpassing that.
前記[I]項で示した成分を有する鋼のスラブを熱延加熱炉に挿入し、加熱する。当該スラブの熱延加熱炉からの抽出温度を1080℃以上とするのは、へげ疵を誘発する鋳片表層の介在物を除するためのスケール生成量を確保するためである。スケール生成量はスケール厚さに換算して0.2mm以上であればよい。また、抽出温度の上限を1190℃とするのは、発銹起点となるMnSやCaSの生成を抑止してTi系炭硫化物(例えばTi4C2S2)を安定化させるためである。本発明の目的とする耐銹性と表面光沢の確保を考慮すると、抽出温度は1140〜1180℃のとすることが好ましい。A steel slab having the component shown in [I] above is inserted into a hot rolling furnace and heated. The extraction temperature of the slab from the hot-rolling furnace is set to 1080 ° C. or more in order to secure a scale generation amount for removing inclusions on the surface of the slab that induces scabs. The scale generation amount may be 0.2 mm or more in terms of scale thickness. In addition, the upper limit of the extraction temperature is set to 1190 ° C. in order to stabilize the Ti-based carbon sulfide (for example, Ti 4 C 2 S 2 ) by suppressing the generation of MnS and CaS as starting points. In consideration of ensuring the weather resistance and surface gloss as the object of the present invention, the extraction temperature is preferably 1140 to 1180 ° C.
熱間圧延後の巻取り温度を500℃以上とするのは、巻取り時の表面疵を抑制するためである。巻取り温度を500℃未満とすると、熱間圧延後の注水により熱延鋼帯の形状不良を招き、コイル展開や通板時に表面疵を誘発する。巻取り温度を700℃以下とするのは、光沢低下を招く内部酸化物や粒界酸化の成長を抑制するためである。700℃超ではTiやPを含む析出物が析出しやすく、耐銹性低下に繋がる恐れがあるからである。本発明の目的とする表面光沢と耐銹性の確保を考慮すると、巻取り温度は550〜650℃とすることが好ましい。 The reason for setting the winding temperature after hot rolling to 500 ° C. or more is to suppress surface flaws during winding. When the coiling temperature is less than 500 ° C., the hot-rolled steel strip causes poor shape of the hot-rolled steel strip, and induces surface flaws when the coil is unfolded or passed. The reason why the coiling temperature is set to 700 ° C. or lower is to suppress the growth of internal oxides and grain boundary oxidation that cause a reduction in gloss. If the temperature exceeds 700 ° C., precipitates containing Ti and P are likely to precipitate, which may lead to a decrease in weather resistance. In consideration of securing the surface gloss and weather resistance which are the objects of the present invention, the winding temperature is preferably 550 to 650 ° C.
熱間圧延で巻き取った後、冷間圧延を行う。このとき、冷間圧延の前に、熱延板焼鈍を実施してもよい。また、冷間圧延は、1回行うか、または2回以上行ってもよい。ただし、2回以上の冷間圧延を行う場合、各冷間圧延の間に中間焼鈍を行う。
熱延板焼鈍を実施する場合は、光沢低下を招く内部酸化物や粒界酸化の成長を抑制するため、焼鈍温度は1050℃以下とすることが好ましい。また焼鈍温度の下限は鋼の再結晶温度(850℃程度)とすることが好ましい。ここで再結晶温度とは、圧延された加工組織から歪の無い新しい結晶粒が形成される温度のことである。
冷間圧延時の中間焼鈍を実施する場合も同様の温度範囲とすることが好ましい。After winding by hot rolling, cold rolling is performed. At this time, hot-rolled sheet annealing may be performed before cold rolling. Further, the cold rolling may be performed once or twice or more. However, when performing cold rolling twice or more, intermediate annealing is performed between each cold rolling.
When hot-rolled sheet annealing is performed, the annealing temperature is preferably set to 1050 ° C. or lower in order to suppress the growth of internal oxides and grain boundary oxidation that cause a decrease in gloss. The lower limit of the annealing temperature is preferably the steel recrystallization temperature (about 850 ° C.). Here, the recrystallization temperature is a temperature at which new crystal grains having no distortion are formed from a rolled processed structure.
The same temperature range is preferable when performing the intermediate annealing at the time of cold rolling.
冷間圧延の条件は特に限定しない。冷間圧延後の仕上げ焼鈍は、表面光沢を考慮して、980℃以下とすることが好ましい。前述したように、焼鈍温度が低いほど内部酸化・粒界酸化が抑制されるため表面光沢を向上させるには有利である。このため、下限は、再結晶温度である850℃とすることが好ましい。酸洗方法は特に規定するものではなく、工業的に常用されている方法で実施しても問題ない。例えば、アルカリソルトバス浸漬+電解酸洗+硝弗酸浸漬、アルカリソルトバス浸漬+電解酸洗があり、電解酸洗は中性塩電解や硝酸電解等を行えばよい。 The conditions for cold rolling are not particularly limited. The finish annealing after cold rolling is preferably 980 ° C. or lower in consideration of surface gloss. As described above, the lower the annealing temperature, the more the internal oxidation and grain boundary oxidation are suppressed, which is advantageous for improving the surface gloss. For this reason, the lower limit is preferably set to 850 ° C. which is the recrystallization temperature. The pickling method is not particularly specified, and there is no problem even if it is carried out by a method commonly used in industry. For example, there are alkaline salt bath immersion + electrolytic pickling + nitric hydrofluoric acid immersion, alkaline salt bath immersion + electrolytic pickling, and the electrolytic pickling may be performed by neutral salt electrolysis or nitric acid electrolysis.
以下、本発明の実施例を説明する。 Examples of the present invention will be described below.
表1の成分を有するフェライト系ステンレス鋼を溶製し、抽出温度1050〜1220℃で熱間圧延を行い、巻取り温度480〜750℃で板厚4.0〜6.0mmの熱延鋼板とした。熱延鋼板は熱延板焼鈍を実施あるいは省略して、1回または中間焼鈍を挟む2回の冷間圧延を行い、0.4〜1.0mm厚の冷延鋼板を製造した。得られた冷延鋼板は、いずれも再結晶が完了する温度870〜1020℃で仕上げ焼鈍を行い、常用の酸洗処理を施して、表面仕様はJIS G 4307に規定されるNo.2B品とした。常用の酸洗処理は、例えば、アルカリソルトバス浸漬(430℃)後、中性塩電解(50℃、Na2SO4)処理でよい。
鋼の成分は、本発明で規定する範囲とそれ以外でも実施した。製造条件は、本発明で限定する条件とそれ以外でも実施した。比較鋼には、SUS430LX(17%Cr−0.3%Ti)を使用した。
The ferritic stainless steel having components shown in Table 1 were melted, subjected to hot rolling at extraction temperature 1 0 50-1220 ° C., hot rolled sheet thickness 4.0~6.0mm at coiling temperature four hundred eighty to seven hundred and fifty ° C. A steel plate was used. The hot-rolled steel sheet was subjected to hot-rolled sheet annealing or omitted, and cold-rolled steel sheet having a thickness of 0.4 to 1.0 mm was manufactured by performing cold rolling twice or twice with intermediate annealing. Each of the obtained cold-rolled steel sheets is subjected to finish annealing at a temperature of 870 to 1020 ° C. at which recrystallization is completed, and subjected to regular pickling treatment, and the surface specification is No. stipulated in JIS G 4307. It was set as 2B goods. The common pickling treatment may be, for example, a neutral salt electrolysis (50 ° C., Na 2 SO 4 ) treatment after immersion in an alkali salt bath (430 ° C.).
The components of the steel were also carried out in the range specified in the present invention and other cases. The manufacturing conditions were the same as those defined in the present invention and other conditions. SUS430LX (17% Cr-0.3% Ti) was used as a comparative steel.
表面光沢度は、JIS Z 8741に規定されている光沢度45°Gloss値(Gs45°)を鋼板の圧延方向(0°)と圧延直角方向(90°)において測定した。耐銹性は、No.2B表面および#600研磨表面の鋼板試料(板厚×100mm角)を作成し、80℃、0.5%NaCl水溶液中168hr浸漬試験とJIS Z 2371に準拠する塩水噴霧試験(168hr連続噴霧試験)により評価した。発銹の程度は、SUS430LXと比較して、しみや点銹がなく良好である場合を「◎」、同等で遜色ない場合を「○」、流れ銹が発生して場合等劣る場合を「×」として評価した。表2に各試験結果をまとめて示す。 The surface glossiness was determined by measuring the glossiness 45 ° Gloss value (Gs45 °) defined in JIS Z 8741 in the rolling direction (0 °) and the perpendicular direction (90 °) of the steel sheet. The weather resistance is No. Steel sheet samples (plate thickness x 100 mm square) on the 2B surface and # 600 polished surface were prepared and immersed in a 168 hr in a 0.5% NaCl aqueous solution at 80 ° C. and a salt spray test in accordance with JIS Z 2371 (168 hr continuous spray test) It was evaluated by. Compared with SUS430LX, the degree of rusting is “◎” when it is good without stains or spots, “◯” when it is comparable and inferior, ". Table 2 summarizes the test results.
表2から、試験番号1〜21は、本発明で限定する成分を全て満足するフェライト系ステンレス鋼である。これら鋼板は、SUS430LXと比較して高い表面光沢度(SUS430LXのGa45°(0°)での光沢度=610以上、Ga45°(90°)での光沢度=520以上)を有し、かつ耐銹性についてもSUS430LXと遜色ない程度あるいはそれを上回る良好なものであることがわかる。 From Table 2, test numbers 1 to 21 are ferritic stainless steels that satisfy all of the components defined in the present invention. These steel sheets have a higher surface glossiness (Glossiness at Ga45 ° (0 °) of SUS430LX = 610 or more, Glossiness at Ga45 ° (90 °) = 520 or more) than SUS430LX, and resistance to SUS430LX. It can also be seen that the fertility is good enough to exceed or exceed that of SUS430LX.
試験番号8、9、15、16は、本発明で規定する成分を有するものの、本発明に係る製造方法(抽出温度、巻取り温度、仕上焼鈍温度)から外れるものである。これら鋼板は、本発明で目標とする耐銹性や光沢度は満足しているが、光沢度が他の本発明例に比べて若干劣るものとなった。 Test Nos. 8, 9, 15, and 16 have components specified by the present invention, but deviate from the production method (extraction temperature, winding temperature , finish annealing temperature ) according to the present invention. These steel sheets satisfied the target weather resistance and glossiness according to the present invention, but the glossiness was slightly inferior to those of the other examples of the present invention.
試験番号22〜29は、本発明で規定する製造方法を実施しているものの、本発明の成分から外れるものである。これら鋼板は、本発明で目標とする表面光沢と耐銹性の両者を兼備することが出来なかった。 Although test numbers 22-29 are implementing the manufacturing method prescribed | regulated by this invention, it remove | deviates from the component of this invention. These steel sheets could not have both the surface gloss and weather resistance targeted by the present invention.
図1および図2に、実施例におけるNb/Ti量と表面光沢度の関係を示す。本発明の目標とする表面光沢であるSUS430LX相当のGs45°(0°)で610以上を、Gs45°(90°)で520以上を得るには、本発明で規定する成分範囲とする1≦Nb/Ti≦3.5とするとよいことが重要である。 1 and 2 show the relationship between the Nb / Ti amount and the surface glossiness in the examples. In order to obtain 610 or more at Gs45 ° (0 °) equivalent to SUS430LX, which is the target surface gloss of the present invention, and 520 or more at Gs45 ° (90 °), the component range specified in the present invention is 1 ≦ Nb It is important that /Ti≦3.5.
本発明によれば、合金コストや製造コストの上昇を招くことなく経済性に優れ、SUS430LXやSUS430J1Lと遜色ない耐銹性を有し、表面光沢を飛躍的に向上した、表面光沢と耐銹性に優れた省合金型のフェライト系ステンレス鋼を得ることができる。 According to the present invention, the surface gloss and the weather resistance are excellent, which is excellent in economic efficiency without causing an increase in alloy costs and manufacturing costs, has a weather resistance comparable to SUS430LX and SUS430J1L, and has dramatically improved the surface gloss. It is possible to obtain an alloy-saving ferritic stainless steel with excellent resistance.
Claims (6)
C:0.001〜0.03%、
Si:0.01〜1.0%、
Mn:0.01〜1.5%、
P:0.005〜0.05%、
S:0.0001〜0.01%、
Cr:12〜16%、
N:0.001〜0.03%、
Nb:0.05〜0.3%未満、
Ti:0.03〜0.15%未満、
Al:0.005〜0.5%、
Sn:0.01〜1.0%、
残部がFeおよび不可避的不純物からなり、
1.5≦Nb/Ti≦3の関係を満たすことを特徴とする表面光沢と耐銹性に優れたフェライト系ステンレス鋼板。 In mass%
C: 0.001 to 0.03%,
Si: 0.01 to 1.0%,
Mn: 0.01 to 1.5%,
P: 0.005 to 0.05%,
S: 0.0001 to 0.01%,
Cr: 12-16%,
N: 0.001 to 0.03%,
Nb: 0.05 to less than 0.3%,
Ti: 0.03 to less than 0.15%,
Al: 0.005 to 0.5%,
Sn: 0.01-1.0%,
The balance consists of Fe and inevitable impurities,
A ferritic stainless steel sheet excellent in surface gloss and weather resistance, characterized by satisfying a relationship of 1.5 ≦ Nb / Ti ≦ 3 .
Ni:0.01〜0.5%、
Cu:0.01〜0.5%、
Mo:0.01〜0.5%、
V:0.01〜0.5%、
Zr:0.01〜0.5%、
Co:0.01〜0.5%、
Mg:0.0001〜0.005%、
B:0.0003〜0.005%、
Ca:0.0003〜0.005%
の1種または2種以上含有していることを特徴とする請求項1に記載の表面光沢と耐銹性に優れたフェライト系ステンレス鋼板。 The stainless steel plate is further in mass%,
Ni: 0.01 to 0.5%,
Cu: 0.01 to 0.5%,
Mo: 0.01 to 0.5%,
V: 0.01-0.5%
Zr: 0.01 to 0.5%,
Co: 0.01 to 0.5%
Mg: 0.0001 to 0.005%,
B: 0.0003 to 0.005%,
Ca: 0.0003 to 0.005%
The ferritic stainless steel sheet having excellent surface gloss and weather resistance according to claim 1, wherein the ferritic stainless steel sheet is excellent in surface gloss and weather resistance.
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- 2011-03-22 KR KR1020127025734A patent/KR101536291B1/en active IP Right Grant
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Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
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JPH10280035A (en) * | 1997-04-11 | 1998-10-20 | Nippon Steel Corp | Production of high purity ferritic stainless hot rolled steel strip excellent in workability and heat resistance |
JP2001288543A (en) * | 2000-04-04 | 2001-10-19 | Nippon Steel Corp | Ferritic stainless steel excellent in surface property and corrosion resistance, and its production method |
JP2004060009A (en) * | 2002-07-30 | 2004-02-26 | Nippon Steel Corp | Ferritic stainless steel sheet having excellent press formability and method for producing the same |
JP2010031315A (en) * | 2008-07-28 | 2010-02-12 | Nippon Steel & Sumikin Stainless Steel Corp | Low alloy type ferritic stainless steel for automotive exhaust system member having excellent corrosion resistance after heating |
Also Published As
Publication number | Publication date |
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EP2554701B1 (en) | 2016-06-29 |
ES2581315T3 (en) | 2016-09-05 |
CN102822373B (en) | 2016-07-06 |
KR101536291B1 (en) | 2015-07-13 |
CN102822373A (en) | 2012-12-12 |
US20130017116A1 (en) | 2013-01-17 |
EP2554701A1 (en) | 2013-02-06 |
JPWO2011122513A1 (en) | 2013-07-08 |
BR112012024625B1 (en) | 2019-01-08 |
EP2554701A4 (en) | 2015-04-29 |
TWI461547B (en) | 2014-11-21 |
WO2011122513A1 (en) | 2011-10-06 |
KR20120127737A (en) | 2012-11-23 |
BR112012024625A2 (en) | 2016-05-31 |
TW201139698A (en) | 2011-11-16 |
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