TWI638055B - Ferrous iron series stainless steel plate - Google Patents
Ferrous iron series stainless steel plate Download PDFInfo
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Abstract
本發明提供一種兼顧表面缺陷之降低與韌性之提高、且耐蝕性優異之肥粒鐵系不銹鋼板。 The present invention provides a ferrous iron-based stainless steel sheet that has both reduced surface defects and improved toughness, and has excellent corrosion resistance.
一種肥粒鐵系不銹鋼板,其特徵在於:以質量%計含有C:0.020%以下、Si:0.05~0.40%、Mn:0.05~1.00%、P:0.040%以下、S:0.030%以下、Al:0.001~0.15%、Cr:20.0~23.0%、Ni:0.01~0.80%、Cu:0.30~0.80%、Ti:0.10~0.50%、Nb:0.010~0.150%、Zr:0.005~0.150%、及N:0.020%以下,且滿足下述(1)式,剩餘部分包含Fe及不可避免之雜質。 A ferrous iron-based stainless steel plate characterized in that it contains, by mass%, C: 0.020% or less, Si: 0.05 to 0.40%, Mn: 0.05 to 1.00%, P: 0.040% or less, S: 0.030% or less, Al : 0.001 to 0.15%, Cr: 20.0 to 23.0%, Ni: 0.01 to 0.80%, Cu: 0.30 to 0.80%, Ti: 0.10 to 0.50%, Nb: 0.010 to 0.150%, Zr: 0.005 to 0.150%, and N : 0.020% or less, satisfying the following formula (1), and the remainder contains Fe and inevitable impurities.
Zr≦Nb≦Ti (1) Zr ≦ Nb ≦ Ti (1)
(再者,(1)式中之Zr、Nb及Ti係指各成分之含量(質量%)) (Further, Zr, Nb, and Ti in the formula (1) refer to the content (% by mass) of each component)
Description
本發明係關於一種耐蝕性優異、表面缺陷較少、且韌性優異之肥粒鐵系不銹鋼板。 The present invention relates to a ferrous iron-based stainless steel plate having excellent corrosion resistance, few surface defects, and excellent toughness.
肥粒鐵系不銹鋼板由於並非大量地含有Ni,故而與沃斯田體(austenite)系不銹鋼板相比係廉價且價格穩定性優異之材料。又,肥粒鐵系不銹鋼板由於耐生銹性優異,故而被用於建築材料、運輸機器、家庭電器及廚房設備等各種用途。 Since the ferrous iron-based stainless steel plate does not contain Ni in a large amount, it is a material that is cheaper than the austenite-based stainless steel plate and has excellent price stability. In addition, the ferrous iron-based stainless steel plate is used in various applications such as building materials, transportation equipment, home appliances, and kitchen equipment because of its excellent rust resistance.
即便於肥粒鐵系不銹鋼板中,SUS443J1(JIS G 4305)亦由於藉由含有20.0~23.0質量%之Cr、0.3~0.8質量%之Cu、進而足夠量之穩定元素(Ti、Nb及Zr),而具有與作為沃斯田體系不銹鋼之SUS304(JIS G 4305、18質量%之Cr-8質量%之Ni)同等之優異之耐蝕性,故而被應用於腐蝕環境尤為嚴重之用途。 Even in the ferrous stainless steel plate, SUS443J1 (JIS G 4305) also contains 20.0 to 23.0% by mass of Cr, 0.3 to 0.8% by mass of Cu, and a sufficient amount of stabilizing elements (Ti, Nb, and Zr). It has the same excellent corrosion resistance as SUS304 (JIS G 4305, 18 mass% Cr-8 mass% Ni), which is a stainless steel of the Wastfield system. Therefore, it is used in corrosive environments.
即便於SUS443J1中,亦通常為主要含有Ti作為穩定元素之SUS443J1。該鋼藉由含有Ti而促進織構之發達,加工性優異。進而,與含有Nb者相比,即便為較低溫度下之冷軋板退火,亦會充分地軟質化,因此,可穿過與普通鋼共通之冷軋板退火酸洗線而進行製造,生產性良好。然而,於含有Ti之SUS443J1中,有於表面產生損害美觀之條紋圖案(表面缺陷)之情況。已知上述條紋圖案係起因於在鑄造時於表面生成之粗大之TiN。又,於含有Ti之SUS443J1中,亦存在韌性較低之問題。其原因在於, 會生成成為優先之破壞起點之粗大的TiN。 Even in SUS443J1, it is usually SUS443J1 mainly containing Ti as a stabilizing element. This steel promotes the development of texture by containing Ti, and is excellent in workability. Furthermore, compared with those containing Nb, even cold-rolled sheet annealing at a lower temperature will be sufficiently softened, so it can be manufactured and produced through the annealing and pickling line of cold-rolled sheet common with ordinary steel Sex is good. However, in SUS443J1 containing Ti, a stripe pattern (surface defect) that impairs the appearance may be generated on the surface. It is known that the above-mentioned stripe pattern results from coarse TiN generated on the surface during casting. In addition, SUS443J1 containing Ti has a problem of low toughness. The reason is that A coarse TiN will be generated, which is the starting point of the preferred destruction.
關於含有Ti之肥粒鐵系不銹鋼之表面缺陷之防止或韌性提高,於專利文獻1或專利文獻2中有記載。 Patent Literature 1 or Patent Literature 2 describes prevention of surface defects or improvement of toughness of a ferritic iron-based stainless steel containing Ti.
於專利文獻1中,揭示有耐麻紋(roping)性優異、而且表面性狀良好之添加Ti之肥粒鐵系不銹鋼之製造方法。於專利文獻1中,藉由對鋼之凝固溫度、澆鑄溫度及TiN析出溫度以成為特定之關係之方式進行控制,而控制於鋼液之澆鑄時點之TiN的析出,從而防止冷軋退火板之表面缺陷。 Patent Document 1 discloses a method for producing a ferritic iron-based stainless steel with added Ti which is excellent in roping resistance and has good surface properties. In Patent Document 1, by controlling the solidification temperature, casting temperature, and TiN precipitation temperature of the steel in a specific relationship, the precipitation of TiN at the time of casting the molten steel is controlled, thereby preventing the cold-rolled annealed plate. Surface defects.
於專利文獻2中,揭示有韌性優異且具有良好之耐蝕性、且生產性及經濟性優異之肥粒鐵系不銹鋼板及其製造方法。於專利文獻2中,藉由使鋼中之氮化物以ZrN之形態存在,而提高熱軋退火板及冷軋退火板之韌性。 Patent Document 2 discloses a ferritic iron-based stainless steel sheet having excellent toughness, good corrosion resistance, and excellent productivity and economy, and a method for producing the same. In Patent Document 2, the toughness of the hot-rolled annealed sheet and the cold-rolled annealed sheet is improved by causing the nitrides in the steel to exist in the form of ZrN.
專利文獻1:日本專利特開平1-118341號公報 Patent Document 1: Japanese Patent Laid-Open No. 1-118341
專利文獻2:日本專利特開2011-214060號公報 Patent Document 2: Japanese Patent Laid-Open No. 2011-214060
近年來,伴隨家用電器之多樣化,要求除了優異之耐蝕性以外,還要兼顧表面之條紋圖案之降低與優異之韌性之兩者之肥粒鐵系不銹鋼板。 In recent years, along with the diversification of household appliances, in addition to excellent corrosion resistance, a ferrous iron-based stainless steel sheet that has both a reduction in a stripe pattern on the surface and an excellent toughness is required.
然而,於專利文獻1所示之方法中,為了獲得鋼坯之等軸晶率之提高效果,故意使TiN析出,因此,無法獲得充分之韌性之提高效果 及表面缺陷之降低效果。又,於專利文獻2所示之方法中,無法充分地抑制鋼中之TiN之生成,從而無法獲得充分之韌性之提高效果及表面缺陷之降低效果。 However, in the method shown in Patent Document 1, in order to obtain the effect of improving the equiaxed crystal ratio of the slab, TiN is intentionally precipitated, and therefore, a sufficient effect of improving toughness cannot be obtained. And the effect of reducing surface defects. Furthermore, in the method shown in Patent Document 2, the generation of TiN in steel cannot be sufficiently suppressed, and thus sufficient effects of improving toughness and reducing effects of surface defects cannot be obtained.
本發明之目的在於提供一種肥粒鐵系不銹鋼板,該肥粒鐵系不銹鋼板係兼顧表面缺陷之降低與韌性之提高,進而即便利用與習知之含有Ti之SUS443J1同等之溫度下之冷軋板退火亦會充分地軟質化,且耐蝕性優異。 The object of the present invention is to provide a ferritic iron-based stainless steel plate, which takes into account the reduction of surface defects and the improvement of toughness, and even uses a cold-rolled plate at the same temperature as the conventional Ti-containing SUS443J1. Annealing is also sufficiently softened and has excellent corrosion resistance.
發明人等針對上述問題,進行了用以兼顧表面缺陷之降低與韌性之提高之綜合性研究。結果發現,藉由針對含有Ti之SUS443J1複合地添加適量之Zr及Nb,能夠不使冷軋板退火溫度上升,而使會招致韌性之下降之TiN之析出形態變化,從而改善含有Ti之SUS443J1之韌性。進而發現,藉由該效果能夠使Ti系中介物細小地分散而析出,從而能夠降低起因於TiN之鋼板之表面缺陷。 The inventors have conducted a comprehensive study in consideration of the above-mentioned problems to reduce both surface defects and toughness. As a result, it was found that by adding appropriate amounts of Zr and Nb to SUS443J1 containing Ti, it is possible to change the precipitation morphology of TiN that causes a decrease in toughness without increasing the annealing temperature of the cold-rolled sheet, thereby improving the SUS443J1 containing Ti. toughness. Furthermore, it has been found that by this effect, Ti-based intermediaries can be finely dispersed and precipitated, so that it is possible to reduce surface defects of the steel sheet caused by TiN.
具體而言,發現藉由針對SUS443J1之肥粒鐵系不銹鋼板之穩定元素(Ti、Nb及Zr),設為將其主成分設為0.10~0.50質量%之Ti、進而以0.010~0.150質量%之範圍含有Ti含量以下之Nb、進而以0.005~0.150質量%之範圍含有Nb含量以下之Zr之組成,能夠利用與穩定元素之組成僅為Ti之情形時同等之溫度下之冷軋板退火而充分地軟質化,進而兼顧表面缺陷之降低與較高韌性之實現。可推測其機制係如下。 Specifically, it was found that, with respect to the stabilizing elements (Ti, Nb, and Zr) of the ferrous iron-based stainless steel plate of SUS443J1, the main component was set to 0.10 to 0.50% by mass of Ti, and then 0.010 to 0.150% by mass. The composition containing Nb below the Ti content and further containing Zr below the Nb content in the range of 0.005 to 0.150% by mass can be annealed with a cold-rolled sheet at the same temperature as when the composition of the stabilizing element is only Ti. Fully softened, and then both the reduction of surface defects and the realization of higher toughness are taken into account. The mechanism is speculated as follows.
藉由在鋼中複合地含有Nb及Zr,而與於單獨添加Ti系之肥粒鐵系不銹鋼中生成之TiN相比,變得尺寸較小之Ti、Zr及Nb之複合碳氮化物((Ti、Zr、Nb)(C、N))分散而析出,從而實現韌性之提高及表面缺陷之降低。 By compositely containing Nb and Zr in steel, the composite carbonitride of Ti, Zr, and Nb becomes smaller in size compared to TiN generated in the ferritic iron-based stainless steel in which Ti is added alone (( Ti, Zr, Nb) (C, N)) are dispersed and precipitated, thereby improving the toughness and reducing the surface defects.
本發明係立足於上述見解者,其主旨構成係如下所述。 The present invention is based on the above-mentioned insights, and its gist structure is as follows.
[1]一種肥粒鐵系不銹鋼板,其特徵在於:以質量%計含有C:0.020%以下、Si:0.05~0.40%、Mn:0.05~1.00%、P:0.040%以下、S:0.030%以下、Al:0.001~0.15%、Cr:20.0~23.0%、Ni:0.01~0.80%、Cu:0.30~0.80%、Ti:0.10~0.50%、Nb:0.010~0.150%、Zr:0.005~0.150%、及N:0.020%以下,且滿足下述(1)式,剩餘部分包含Fe及不可避免之雜質。 [1] A ferrous iron-based stainless steel plate, characterized in that it contains C: 0.020% or less, Si: 0.05 ~ 0.40%, Mn: 0.05 ~ 1.00%, P: 0.040% or less, and S: 0.030% by mass% Below, Al: 0.001 to 0.15%, Cr: 20.0 to 23.0%, Ni: 0.01 to 0.80%, Cu: 0.30 to 0.80%, Ti: 0.10 to 0.50%, Nb: 0.010 to 0.150%, Zr: 0.005 to 0.150% , And N: 0.020% or less, and satisfying the following formula (1), the remainder contains Fe and inevitable impurities.
Zr≦Nb≦Ti (1) Zr ≦ Nb ≦ Ti (1)
(再者,(1)式中之Zr、Nb及Ti係指各成分之含量(質量%)) (Further, Zr, Nb, and Ti in the formula (1) refer to the content (% by mass) of each component)
[2]如[1]之肥粒鐵系不銹鋼板,其特徵在於:進而,以質量%計含有選自Co:0.01~0.50%、Mo:0.01~0.30%及W:0.01~0.50%中之1種或2種以上。 [2] The ferrous iron-based stainless steel plate according to [1], further characterized by containing, in mass%, a member selected from the group consisting of Co: 0.01 to 0.50%, Mo: 0.01 to 0.30%, and W: 0.01 to 0.50% 1 or more.
[3]如[1]或[2]之肥粒鐵系不銹鋼板,其特徵在於:進而以質量%計含有選自V:0.01~0.50%、B:0.0003~0.0030%、Mg:0.0005~0.0100%、Ca:0.0003~0.0030%、Y:0.001~0.20%及稀土類金屬(REM,Rare Earth Metals):0.001~0.10%中之1種或2種以上。 [3] The ferrous iron-based stainless steel plate according to [1] or [2], further characterized by containing, in mass%, a member selected from the group consisting of V: 0.01 to 0.50%, B: 0.0003 to 0.0030%, and Mg: 0.0005 to 0.0100. %, Ca: 0.0003 ~ 0.0030%, Y: 0.001 ~ 0.20%, and rare earth metals (REM, Rare Earth Metals): 0.001 ~ 0.10%, one or more kinds.
[4]如[1]至[3]中任一項之肥粒鐵系不銹鋼板,其特徵在於:進而以質量%計含有選自Sn:0.001~0.50%及Sb:0.001~0.50%中之1種或2種。 [4] The ferrous iron-based stainless steel plate according to any one of [1] to [3], further comprising, in mass%, a member selected from the group consisting of Sn: 0.001 to 0.50% and Sb: 0.001 to 0.50% 1 or 2 species.
根據本發明,可獲得耐蝕性優異、表面缺陷較少、進而韌性優異之肥粒鐵系不銹鋼板。 According to the present invention, a ferrous iron-based stainless steel sheet having excellent corrosion resistance, few surface defects, and excellent toughness can be obtained.
又,利用與穩定元素之組成僅為Ti之情形時同等之溫度下之冷軋板退火即可充分地軟質化,因此,肥粒鐵系不銹鋼板之生產性較高。 In addition, the cold-rolled sheet can be sufficiently softened by annealing at the same temperature as when the composition of the stabilizing element is only Ti, so that the ferritic iron-based stainless steel sheet has high productivity.
圖1係表示於Zr≦Nb之條件下,Ti及Nb含量對韌性及表面缺陷之量給予之影響之圖。 Figure 1 is a graph showing the effects of Ti and Nb contents on the amount of toughness and surface defects under the condition of Zr ≦ Nb.
圖2係表示於Nb≦Ti之條件下,Nb及Zr之含量對韌性及表面缺陷之量給予之影響之圖。 FIG. 2 is a graph showing the effect of the content of Nb and Zr on the amount of toughness and surface defects under the condition of Nb ≦ Ti.
以下,對本發明之實施形態進行說明。再者,本發明並不限定於以下之實施形態。 Hereinafter, embodiments of the present invention will be described. The present invention is not limited to the following embodiments.
本發明之肥粒鐵系不銹鋼板之成分組成係以質量%計含有C:0.020%以下、Si:0.05~0.40%、Mn:0.05~1.00%、P:0.040%以下、S:0.030%以下、Al:0.001~0.15%、Cr:20.0~23.0%、Ni:0.01~0.80%、Cu:0.30~0.80%、Ti:0.10~0.50%、Nb:0.010~0.150%、Zr:0.005~0.150%、及N:0.020%以下,且滿足下述(1)式,剩餘部分包含Fe及不可避免之雜質。 The composition of the ferrous iron-based stainless steel plate of the present invention contains C: 0.020% or less, Si: 0.05 to 0.40%, Mn: 0.05 to 1.00%, P: 0.040% or less, S: 0.030% or less by mass%, Al: 0.001 to 0.15%, Cr: 20.0 to 23.0%, Ni: 0.01 to 0.80%, Cu: 0.30 to 0.80%, Ti: 0.10 to 0.50%, Nb: 0.010 to 0.150%, Zr: 0.005 to 0.150%, and N: 0.020% or less, satisfying the following formula (1), and the remainder contains Fe and inevitable impurities.
Zr≦Nb≦Ti (1) Zr ≦ Nb ≦ Ti (1)
再者,(1)式中之Zr、Nb及Ti係指各成分之含量(質量%)。 In addition, Zr, Nb, and Ti in the formula (1) refer to the content (% by mass) of each component.
又,上述成分組成亦可進而以質量%計含有選自Co:0.01~0.50%、Mo:0.01~0.30%及W:0.01~0.50%中之1種或2種以上。 Further, the above-mentioned component composition may further contain one or two or more kinds selected from Co: 0.01 to 0.50%, Mo: 0.01 to 0.30%, and W: 0.01 to 0.50% in mass%.
又,上述成分組成亦可進而以質量%計含有選自V:0.01~0.50%、B:0.0003~0.0030%、Mg:0.0005~0.0100%、Ca:0.0003~0.0030%、Y:0.001~0.20%及REM(稀土類金屬):0.001~0.10%中之1種或2種以上。 Further, the above-mentioned component composition may further contain, in mass%, selected from the group consisting of V: 0.01 to 0.50%, B: 0.0003 to 0.0030%, Mg: 0.0005 to 0.0100%, Ca: 0.0003 to 0.0030%, Y: 0.001 to 0.20%, and REM (rare earth metals): 0.001 to 0.10% of one or more.
又,上述成分組成亦可進而以質量%計含有選自Sn:0.001~0.50%及Sb:0.001~0.50%中之1種或2種。 Further, the above-mentioned component composition may further contain one or two selected from the group consisting of Sn: 0.001 to 0.50% and Sb: 0.001 to 0.50% in mass%.
以下,對各成分進行說明。指成分之含量之「%」只要並無特別限定則指質量%。 Hereinafter, each component is demonstrated. "%", Which refers to the content of the ingredients, means% by mass as long as it is not particularly limited.
C係對於提高鋼之強度較為有效之元素。該效果可藉由將C含量設為0.001%以上而獲得。但是,若C含量超過0.020%,則耐蝕性及加工性顯著下降。因此,C含量係設為0.020%以下。又,理想的是將C含量設為0.015%以下。進而理想的是0.010%以下。 C is an element that is more effective for improving the strength of steel. This effect can be obtained by setting the C content to 0.001% or more. However, if the C content exceeds 0.020%, the corrosion resistance and processability are significantly reduced. Therefore, the C content is set to 0.020% or less. The C content is desirably 0.015% or less. Furthermore, it is preferably 0.010% or less.
Si係作為脫氧劑而有用之元素。該效果可藉由將Si含量設為0.05%以上而獲得。但是,若Si含量超過0.40%,則鋼係硬質化而加工性下降。又,若Si含量超過0.40%,則於熱軋時具有潤滑效果之鋼坯上表面之銹皮(scale)之生成被抑制,而使表面缺陷變大。因此,Si含量係限定於0.05~0.40%之範圍。更佳為0.05~0.25%之範圍。關於Si含量之下限,進而較佳為0.08%以上。關於Si含量之上限,進而較佳為0.15%以下。 Si is an element useful as a deoxidizer. This effect can be obtained by setting the Si content to 0.05% or more. However, if the Si content exceeds 0.40%, the steel system will be hardened and the workability will decrease. In addition, if the Si content exceeds 0.40%, generation of scale on the upper surface of the slab having a lubricating effect during hot rolling is suppressed, and surface defects become large. Therefore, the Si content is limited to the range of 0.05 to 0.40%. A more preferable range is 0.05 to 0.25%. The lower limit of the Si content is more preferably 0.08% or more. The upper limit of the Si content is more preferably 0.15% or less.
Mn具有脫氧作用。該效果可藉由將Mn含量設為0.05%以上而獲得。另一方面,若Mn含量超過1.00%,則會促進MnS之析出及粗大化,從而耐蝕性下降。因此,Mn含量係限定於0.05~1.00%之範圍。關於下限,更佳之Mn含量為0.10%以上,進而較佳為0.15%以上。關於上限,更佳之Mn含量係未滿0.30%,進而較佳為0.25%以下。 Mn has a deoxidizing effect. This effect can be obtained by setting the Mn content to 0.05% or more. On the other hand, if the Mn content exceeds 1.00%, the precipitation and coarsening of MnS are promoted, and the corrosion resistance is reduced. Therefore, the Mn content is limited to the range of 0.05 to 1.00%. Regarding the lower limit, a more preferable Mn content is 0.10% or more, and still more preferably 0.15% or more. Regarding the upper limit, a more preferable Mn content is less than 0.30%, and more preferably 0.25% or less.
P係使耐蝕性下降之元素。又,因P於晶界偏析而導致熱加工性下降。因此,P含量係理想為儘可能較低,設為0.040%以下。較佳為0.030%以下。 P is an element that reduces corrosion resistance. In addition, segregation of P at the grain boundaries causes a decrease in hot workability. Therefore, the P content is preferably as low as possible, and is set to 0.040% or less. It is preferably 0.030% or less.
S係與Mn形成析出物MnS。該MnS與不銹鋼母材之界面成為蝕孔之起點,使耐蝕性下降。因此,S含量係理想為較低,設為0.030%以下。較佳為設為0.020%以下。 S system and Mn form a precipitate MnS. The interface between the MnS and the stainless steel base material becomes the starting point of pitting, which reduces the corrosion resistance. Therefore, the S content is preferably as low as 0.030% or less. The content is preferably 0.020% or less.
Al係用於脫氧而較為有效之元素。該效果可藉由Al含量為0.001%以上而獲得。另一方面,若Al含量超過0.15%,則於熱軋時具有潤滑效果之鋼坯上表面之銹皮之生成被抑制,而使表面缺陷變多。因此,Al含量係限定於0.001~0.15%之範圍。關於下限,較佳之Al含量為0.005%以上,更佳為0.01%以上。關於上限,較佳之Al含量為0.10%以下,進而較佳為0.05%以下。 Al is an effective element for deoxidation. This effect can be obtained when the Al content is 0.001% or more. On the other hand, if the Al content exceeds 0.15%, generation of scale on the upper surface of the slab having a lubricating effect during hot rolling is suppressed, and surface defects increase. Therefore, the Al content is limited to the range of 0.001 to 0.15%. Regarding the lower limit, the Al content is preferably 0.005% or more, and more preferably 0.01% or more. The upper limit is preferably 0.10% or less, and more preferably 0.05% or less.
Cr係於表面形成鈍態皮膜而提高耐蝕性之元素。若Cr含量未滿20.0%,則無法獲得充分之耐蝕性。另一方面,若Cr含量超過23.0%,則變得易因σ相或475℃脆性之影響而韌性下降。因此,Cr含量係設為20.0~23.0%。關於下限,較佳之Cr含量為20.5%以上。關於上限,較佳之Cr含量為22.0%以下,進而較佳為21.5%以下。 Cr is an element that forms a passive film on the surface to improve corrosion resistance. If the Cr content is less than 20.0%, sufficient corrosion resistance cannot be obtained. On the other hand, when the Cr content exceeds 23.0%, the toughness tends to decrease due to the influence of the σ phase or the brittleness at 475 ° C. Therefore, the Cr content is set to 20.0 to 23.0%. Regarding the lower limit, the preferable Cr content is 20.5% or more. Regarding the upper limit, the preferred Cr content is 22.0% or less, and more preferably 21.5% or less.
Ni係抑制由酸引起之陽極反應而即便於更低之pH值亦能夠維持鈍態之元素。即,Ni係提高耐間隙腐蝕性之效果,顯著地抑制活性溶解狀態下之腐蝕之進展而提高耐蝕性。該效果可藉由Ni含量為0.01%以上而獲得。另一方面,若Ni含量超過0.80%,則鋼硬質化而其加工性下降。因此,Ni含量係限定於0.01~0.80%之範圍。關於下限,較佳之Ni含量為0.05%以上,進而較佳為0.10%以上。關於上限,較佳之Ni含量為0.40%以下,進而較佳為0.25%以下。 Ni is an element that suppresses the anode reaction caused by acid and can maintain a passive state even at a lower pH value. That is, the Ni-based effect of improving the interstitial corrosion resistance significantly suppresses the progress of corrosion in an active dissolved state and improves the corrosion resistance. This effect can be obtained when the Ni content is 0.01% or more. On the other hand, when the Ni content exceeds 0.80%, the steel is hardened and its workability is reduced. Therefore, the Ni content is limited to the range of 0.01 to 0.80%. Regarding the lower limit, the Ni content is preferably 0.05% or more, and more preferably 0.10% or more. Regarding the upper limit, the Ni content is preferably 0.40% or less, and more preferably 0.25% or less.
Cu係強化鈍態皮膜而提高耐蝕性之元素。另一方面,若過量地添加Cu,則變得ε-Cu易析出,從而耐蝕性下降。因此,Cu含量係設為0.30~0.80%。關於下限,較佳之Cu含量為0.35%以上,進而較佳為0.40%以上。關於上限,較佳之Cu含量為0.60%以下,進而較佳為0.45%以下。 Cu is an element that strengthens the passive film and improves the corrosion resistance. On the other hand, when Cu is excessively added, ε-Cu is easily precipitated, and the corrosion resistance is reduced. Therefore, the Cu content is set to 0.30 to 0.80%. Regarding the lower limit, the Cu content is preferably 0.35% or more, and more preferably 0.40% or more. Regarding the upper limit, the Cu content is preferably 0.60% or less, and more preferably 0.45% or less.
Ti係固定C及N而防止Cr碳氮化物造成之敏化、而使耐蝕性提高之元素。但是,因Ti添加而生成之TiN會招致韌性下降。如下所述,於本發明中,藉由Nb與Zr之複合效應而抑制上述韌性下降。利用Ti所得之耐蝕性提高效果係藉由Ti含量為0.10%以上而獲得。另一方面,若Ti含量超過0.50%,則不銹鋼板硬質化,加工性下降。又,若Ti含量超過0.50%,則變得即便藉由Nb或Zr之添加亦難以進行Ti系中介物之析出形態控制,表面品質下降。因此,Ti含量係設為0.10~0.50% 之範圍。關於下限,較佳之Ti含量為0.15%以上,進而較佳為0.18%以上。關於上限,較佳之Ti含量為0.35%以下,進而較佳為0.26%以下。 Ti is an element that fixes C and N, prevents sensitization by Cr carbonitride, and improves corrosion resistance. However, TiN generated by Ti addition causes a decrease in toughness. As described below, in the present invention, the aforementioned reduction in toughness is suppressed by the composite effect of Nb and Zr. The effect of improving the corrosion resistance by Ti is obtained when the Ti content is 0.10% or more. On the other hand, when the Ti content exceeds 0.50%, the stainless steel plate is hardened, and workability is reduced. In addition, if the Ti content exceeds 0.50%, it becomes difficult to control the precipitation form of the Ti-based intermediary even with the addition of Nb or Zr, and the surface quality decreases. Therefore, the Ti content is set to 0.10 to 0.50%. Range. Regarding the lower limit, the preferred Ti content is 0.15% or more, and more preferably 0.18% or more. Regarding the upper limit, the preferred Ti content is 0.35% or less, and more preferably 0.26% or less.
Nb係與Ti同樣地固定C及N而防止由Cr碳氮化物所致之敏化從而使耐蝕性提高之元素。進而,Nb係藉由與下述之Zr之複合效應而使韌性提高,從而抑制表面缺陷之產生。該效果可藉由Nb含量為0.010%以上而獲得。另一方面,若Nb含量超過0.150%,則不銹鋼板硬質化而加工性下降。又,若Nb含量超過0.150%,則會招致再結晶溫度之上升,製造性下降。因此,Nb含量係設為0.010~0.150%之範圍。關於下限,較佳之Nb含量為0.030%以上,進而較佳為0.070%以上。關於上限,較佳之Nb含量係未滿0.100%,進而較佳為0.090%以下。 Nb is an element that fixes C and N similarly to Ti, prevents sensitization by Cr carbonitride, and improves corrosion resistance. Furthermore, Nb improves toughness by a compound effect with Zr described below, thereby suppressing the occurrence of surface defects. This effect can be obtained when the Nb content is 0.010% or more. On the other hand, when the Nb content exceeds 0.150%, the stainless steel plate becomes hard and workability is reduced. If the Nb content exceeds 0.150%, the recrystallization temperature will increase, and the manufacturability will decrease. Therefore, the Nb content is set in the range of 0.010 to 0.150%. Regarding the lower limit, the Nb content is preferably 0.030% or more, and more preferably 0.070% or more. Regarding the upper limit, the Nb content is preferably less than 0.100%, and more preferably 0.090% or less.
Zr係與Ti同樣地固定C及N而防止由Cr碳氮化物所致之敏化從而使耐蝕性提高之元素。進而,Zr係藉由與下述之Nb之複合效應而使韌性提高,從而抑制表面缺陷之產生。為了獲得該等效果,必須含有0.005%以上之Zr。另一方面,若Zr含量超過0.150%,則於表面析出Zr系中介物,而會招致表面缺陷之增大。因此,Zr含量係限定於0.005~0.150%之範圍。關於下限,較佳之Zr含量為0.010%以上,進而較佳為0.030%以上。關於上限,較佳之Zr含量係未滿0.100%,進而較佳為0.080%以下。 Zr is an element that fixes C and N like Ti, prevents sensitization by Cr carbonitride, and improves corrosion resistance. Furthermore, Zr improves toughness by a compound effect with Nb described below, thereby suppressing the occurrence of surface defects. In order to obtain these effects, Zr must be contained in an amount of 0.005% or more. On the other hand, if the Zr content exceeds 0.150%, Zr-based intermediaries are precipitated on the surface, and an increase in surface defects is caused. Therefore, the Zr content is limited to the range of 0.005 to 0.150%. Regarding the lower limit, the Zr content is preferably 0.010% or more, and more preferably 0.030% or more. Regarding the upper limit, the preferred Zr content is less than 0.100%, and more preferably 0.080% or less.
於本發明中發現,藉由對僅含有Ti作為穩定元素之SUS443J1複合地添加Nb及Zr,利用與穩定元素之組成僅為Ti之情形時同 等之溫度下之冷軋板退火即可充分地軟質化,進而,抑制表面缺陷之產生,並且提高韌性。具體而言,發現藉由將SUS443J1之穩定元素(Ti、Nb及Zr)於下述(1)式之限制下,設為含有0.10~0.50%之Ti、0.010~0.150%之Nb、及0.005~0.150%之Zr之成分組成,能夠利用與穩定元素之組成僅為Ti之情形時同等之溫度下的冷軋板退火而充分地軟質化,進而兼顧降低表面缺陷之產生與高韌性之實現。可推測其機制係取決於以下。 It has been found in the present invention that by adding Nb and Zr to SUS443J1 containing only Ti as a stabilizing element in combination, the use is the same as when the composition of the stabilizing element is only Ti. Annealing the cold-rolled sheet at such a temperature can sufficiently soften, further suppress the occurrence of surface defects, and improve toughness. Specifically, it was found that by stabilizing the elements (Ti, Nb, and Zr) of SUS443J1 within the limits of the following formula (1), it was set to contain 0.10 to 0.50% of Ti, 0.010 to 0.150% of Nb, and 0.005 to The composition of Zr of 0.150% can be fully softened by annealing a cold-rolled sheet at the same temperature as when the composition of the stabilizing element is only Ti, thereby achieving both reduction of surface defects and realization of high toughness. It is speculated that the mechanism depends on the following.
可認為,藉由在鋼中複合地含有Nb及Zr,而與於單獨添加Ti系肥粒鐵系不銹鋼中生成之TiN相比,變得尺寸較小之Ti、Zr及Nb之複合碳氮化物((Ti、Zr、Nb)(C、N))係分散而析出,而實現韌性提高及表面缺陷產生之降低。為了充分地生成上述((Ti、Zr、Nb)(C、N)),必須滿足下述(1)式。 It is considered that the composite carbonitride of Ti, Zr, and Nb becomes smaller in size as compared with TiN produced by adding Ti-based ferritic iron-based stainless steel by compositely containing Nb and Zr in steel. ((Ti, Zr, Nb) (C, N)) is dispersed and precipitated, thereby realizing improvement in toughness and reduction in surface defects. In order to sufficiently generate the above-mentioned ((Ti, Zr, Nb) (C, N)), the following formula (1) must be satisfied.
Zr≦Nb≦Ti (1) Zr ≦ Nb ≦ Ti (1)
再者,(1)式中之Zr、Nb及Ti係指各成分之含量(質量%)。 In addition, Zr, Nb, and Ti in the formula (1) refer to the content (% by mass) of each component.
關於Ti與Nb之關係,較佳為Ti≧1.5Nb,進而較佳為Ti≧2Nb。關於Nb與Zr之關係,較佳為Nb≧1.3Zr,進而較佳為Nb≧1.5Zr。 The relationship between Ti and Nb is preferably Ti ≧ 1.5Nb, and more preferably Ti ≧ 2Nb. The relationship between Nb and Zr is preferably Nb ≧ 1.3Zr, and more preferably Nb ≧ 1.5Zr.
N係不可避免地會混入至鋼中之元素。但是,若N含量超過0.020%,則耐蝕性及加工性顯著下降。因此,N含量係設為0.020%以下。更佳為0.015%以下。 N is an element that is inevitably mixed into steel. However, if the N content exceeds 0.020%, the corrosion resistance and processability are significantly reduced. Therefore, the N content is set to 0.020% or less. It is more preferably 0.015% or less.
以上,針對基本成分進行了說明,但如上所述,於本發明中除此以外亦可適當含有以下所述之元素。 The basic components have been described above, but as described above, the following elements may be appropriately contained in the present invention in addition to the above.
Co係提高不銹鋼之耐間隙腐蝕性之元素。該效果係藉由Co含量為0.01%以上而獲得。但是,若其含量超過0.50%,則該效果係飽和,進而加工性下降。因此,於添加Co之情形時,將Co含量設為0.01~0.50%。關於下限,較佳之Co含量為0.02%以上,進而較佳為0.03%以上。關於上限,較佳之Co含量為0.30%以下,進而較佳為0.10%以下。 Co is an element that improves the interstitial corrosion resistance of stainless steel. This effect is obtained when the Co content is 0.01% or more. However, when the content exceeds 0.50%, the effect is saturated, and the workability is further reduced. Therefore, when Co is added, the Co content is set to 0.01 to 0.50%. Regarding the lower limit, the Co content is preferably 0.02% or more, and more preferably 0.03% or more. Regarding the upper limit, the Co content is preferably 0.30% or less, and more preferably 0.10% or less.
Mo具有提高不銹鋼之耐間隙腐蝕性之效果。該效果係藉由Mo含量為0.01%以上之含量而獲得。但是,若Mo含量超過0.30%,則該效果飽和,進而生成粗大之金屬間化合物而使韌性下降。因此,於添加Mo之情形時,將Mo含量設為0.01~0.30%。關於下限,較佳之Mo含量為0.02%以上,進而較佳為0.03%以上。關於上限,較佳之Mo含量為0.20%以下,進而較佳為0.10%以下。 Mo has the effect of improving the interstitial corrosion resistance of stainless steel. This effect is obtained with a Mo content of 0.01% or more. However, when the Mo content exceeds 0.30%, the effect is saturated, and coarse intermetallic compounds are formed, which reduces the toughness. Therefore, when Mo is added, the Mo content is set to 0.01 to 0.30%. Regarding the lower limit, the Mo content is preferably 0.02% or more, and more preferably 0.03% or more. With regard to the upper limit, the Mo content is preferably 0.20% or less, and more preferably 0.10% or less.
W係提高不銹鋼之耐間隙腐蝕性之元素。該效果係藉由W含量為0.01%以上而獲得。但是,若其含量超過0.50%,則該效果飽和,進而加工性下降。因此,於添加W之情形時,將W含量設為0.01~0.50%。關於下限,較佳之W含量為0.02%以上,進而較佳為0.03%以上。關於上限,較佳之W含量為0.30%以下,進而較佳為0.10%以下。 W is an element that improves the interstitial corrosion resistance of stainless steel. This effect is obtained when the W content is 0.01% or more. However, when the content exceeds 0.50%, the effect is saturated, and the workability is further reduced. Therefore, when W is added, the W content is set to 0.01 to 0.50%. Regarding the lower limit, the W content is preferably 0.02% or more, and more preferably 0.03% or more. Regarding the upper limit, the W content is preferably 0.30% or less, and more preferably 0.10% or less.
V係提高不銹鋼之耐間隙腐蝕性之元素。該效果可藉由V含量為 0.01%以上而獲得。但是,若其含量超過0.50%,則該效果飽和,進而加工性下降。因此,於添加V之情形時,將V含量設為0.01~0.50%。更佳為0.01~0.30%之範圍。進而較佳為0.01~0.10%之範圍。 V is an element that improves the interstitial corrosion resistance of stainless steel. This effect can be achieved by the V content as Obtained above 0.01%. However, when the content exceeds 0.50%, the effect is saturated, and the workability is further reduced. Therefore, when V is added, the V content is set to 0.01 to 0.50%. A more preferable range is 0.01 to 0.30%. It is more preferably in the range of 0.01 to 0.10%.
B係提高熱加工性或二次加工性之元素,B係添加於添加Ti之鋼中較為有效。該效果係藉由B含量為0.0003%以上而獲得。另一方面,若B含量超過0.0030%,則韌性下降。因此,於添加B之情形時將B含量設為0.0003~0.0030%之範圍。關於下限,較佳之B含量為0.0015%以上。關於上限,較佳之B含量為0.0025%以下。 B is an element that improves hot workability or secondary workability. B is more effective when added to Ti-added steel. This effect is obtained when the B content is 0.0003% or more. On the other hand, if the B content exceeds 0.0030%, the toughness decreases. Therefore, when B is added, the B content is set to the range of 0.0003 to 0.0030%. Regarding the lower limit, the preferable B content is 0.0015% or more. Regarding the upper limit, the preferred B content is 0.0025% or less.
Mg係於鋼液中與Al一併形成Mg氧化物而作為脫氧劑發揮作用。該效果係藉由Mg含量為0.0005%以上而獲得。另一方面,若Mg含量超過0.0100%,則鋼之韌性下降而製造性下降。因此,於添加Mg之情形時,將Mg含量限定於0.0005~0.0100%之範圍。關於下限,較佳之Mg含量為0.0010%以上。關於上限,較佳之Mg含量為0.0050%以下,進而較佳為0.0030%以下。 Mg forms a Mg oxide together with Al in the molten steel, and functions as a deoxidizer. This effect is obtained when the Mg content is 0.0005% or more. On the other hand, if the Mg content exceeds 0.0100%, the toughness of the steel decreases and the manufacturability decreases. Therefore, when Mg is added, the Mg content is limited to the range of 0.0005 to 0.0100%. Regarding the lower limit, the preferable Mg content is 0.0010% or more. Regarding the upper limit, the Mg content is preferably 0.0050% or less, and more preferably 0.0030% or less.
Ca係提高熱加工性之元素。該效果可藉由Ca含量為0.0003%以上而獲得。另一方面,若Ca含量超過0.0030%,則鋼之韌性下降。又,因CaS之析出而耐蝕性亦下降。因此,於添加Ca之情形時,將Ca含量限定於0.0003~0.0030%之範圍。關於下限,較佳之Ca含量為0.001% 以上。關於上限,較佳之Ca含量為0.002%以下。 Ca is an element that improves hot workability. This effect can be obtained when the Ca content is 0.0003% or more. On the other hand, if the Ca content exceeds 0.0030%, the toughness of the steel decreases. In addition, corrosion resistance is also reduced due to precipitation of CaS. Therefore, when Ca is added, the Ca content is limited to the range of 0.0003 to 0.0030%. Regarding the lower limit, the preferred Ca content is 0.001% the above. Regarding the upper limit, the preferable Ca content is 0.002% or less.
Y係降低鋼液之黏度下降、提高潔淨度之元素。該效果可藉由Y含量為0.001%以上而獲得。另一方面,若Y含量超過0.20%,則該效果飽和,進而加工性下降。因此,於添加Y之情形時,Y含量係限定於0.001~0.20%之範圍。更佳為0.001~0.10%之範圍。 Y is an element that reduces the viscosity of molten steel and improves the cleanliness. This effect can be obtained when the Y content is 0.001% or more. On the other hand, when the Y content exceeds 0.20%, the effect is saturated, and the workability is further reduced. Therefore, when Y is added, the Y content is limited to the range of 0.001 to 0.20%. A more preferable range is 0.001 to 0.10%.
REM(稀土類金屬:La、Ce、Nd等原子序號57~71之元素)係提高耐高溫氧化性之元素。該效果可藉由REM含量為0.001%以上而獲得。另一方面,若REM含量超過0.10%,則不僅該效果飽和,而且於熱軋時會產生表面缺陷。因此,於添加REM之情形時,將REM含量限定於0.001~0.10%之範圍。關於下限,較佳之REM含量為0.005%以上。關於上限,較佳之REM含量為0.05%以下。 REM (rare earth metals: elements with atomic numbers 57 to 71 such as La, Ce, Nd) is an element that improves high temperature oxidation resistance. This effect can be obtained when the REM content is 0.001% or more. On the other hand, when the REM content exceeds 0.10%, not only the effect is saturated, but also surface defects are generated during hot rolling. Therefore, when REM is added, the REM content is limited to the range of 0.001 to 0.10%. Regarding the lower limit, a preferable REM content is 0.005% or more. Regarding the upper limit, a preferable REM content is 0.05% or less.
Sn係於提高因於輥軋時之變形帶生成之促進而引起之起皺(ridging)方面較為有效。該效果係藉由Sn之含量為0.001%以上而獲得。但是,若Sn之含量超過0.50%,則不僅該效果飽和,而且進而加工性下降。因此,於添加Sn之情形時,將其含量設為0.001~0.50%。關於下限,較佳之Sn含量為0.003%以上。關於上限,較佳之Sn含量為0.20%以下。 Sn is effective in improving the ridging caused by the promotion of the formation of deformed bands during rolling. This effect is obtained when the content of Sn is 0.001% or more. However, when the content of Sn exceeds 0.50%, not only the effect is saturated, but also the workability is lowered. Therefore, when Sn is added, its content is set to 0.001 to 0.50%. Regarding the lower limit, a preferable Sn content is 0.003% or more. Regarding the upper limit, a preferable Sn content is 0.20% or less.
Sb係於藉由在輥軋時促進變形帶生成而提高起皺之方面較為有效。該效果係藉由Sb之含量為0.001%以上而獲得。但是,若Sb之含量超過0.50%,則不僅該效果飽和,而且進而加工性下降。因此,於添加Sb之情形時,將其含量設為0.001~0.50%。關於下限,較佳之Sb含量為0.003%以上,關於上限,較佳之Sb含量為0.20%以下。 Sb is effective in improving wrinkles by promoting the formation of deformed bands during rolling. This effect is obtained when the content of Sb is 0.001% or more. However, when the content of Sb exceeds 0.50%, not only the effect is saturated, but also the workability is lowered. Therefore, when Sb is added, its content is set to 0.001 to 0.50%. Regarding the lower limit, the preferred Sb content is 0.003% or more, and as for the upper limit, the preferred Sb content is 0.20% or less.
除以上成分以外之剩餘部分係Fe及不可避免之雜質。此處所謂之不可避免之雜質之代表例有H、O(氧)、Zn、Ga、Ge、As、Ag、In、Hf、Ta、Re、Os、Ir、Pt、Au、Pb等。該等元素中,可在0.05%以下之範圍包含H及O(氧)。關於其他元素,係可在0.3%以下之範圍包含其他元素。 The remainder other than the above components are Fe and inevitable impurities. Representative examples of the inevitable impurities referred to here include H, O (oxygen), Zn, Ga, Ge, As, Ag, In, Hf, Ta, Re, Os, Ir, Pt, Au, Pb, and the like. Among these elements, H and O (oxygen) may be contained in a range of 0.05% or less. Regarding other elements, other elements may be included in a range of 0.3% or less.
其次,對本發明之肥粒鐵系不銹鋼板之較佳之製造方法進行說明。藉由轉爐、電爐、及真空熔解爐等公知之方法對上述成分組成之鋼進行熔製,並藉由連續鑄造法或鑄錠-分錠法而製成鋼素材(鋼坯)。於將該鋼素材加熱至1000℃~1200℃後,於將完工溫度設為700℃~1000℃之條件下,以成為板厚2.0mm~5.0mm之方式進行熱軋。將以此方式製作之熱軋板於800℃~1100℃之溫度下進行退火並進行酸洗,其次,進行冷軋,並於700℃~1000℃之溫度下進行冷軋板退火。於冷軋板退火後進行酸洗而去除銹皮。亦可對已去除銹皮之冷軋板進行表皮輥軋(skin pass rolling)。 Next, a preferred method for manufacturing the ferrous iron-based stainless steel plate of the present invention will be described. The steel with the above-mentioned composition is melted by a known method such as a converter, an electric furnace, and a vacuum melting furnace, and a steel material (slab) is produced by a continuous casting method or an ingot-split method. After heating this steel material to 1000 ° C. to 1200 ° C., hot rolling is performed so as to have a sheet thickness of 2.0 mm to 5.0 mm under the conditions of a completion temperature of 700 ° C. to 1000 ° C. The hot-rolled sheet produced in this way is annealed and pickled at a temperature of 800 ° C to 1100 ° C, followed by cold rolling, and annealed at a temperature of 700 ° C to 1000 ° C. After the cold-rolled sheet is annealed, pickling is performed to remove scale. Skin pass rolling may also be performed on the cold-rolled sheet from which the scale has been removed.
又,本發明並非僅限於如上所述之冷軋板製品,製成熱軋板製品亦有效。 In addition, the present invention is not limited to the cold-rolled sheet products described above, and it is also effective to make hot-rolled sheet products.
於將具有表1(將表1-1與表1-2合起來作為表1)、表2(將表2-1與表2-2合起來作為表2)、及表3(將表3-1與表3-2合起來作為表3)所示之組成之肥粒鐵系不銹鋼熔製成100kg鋼錠後,加熱至1200℃之溫度而 進行熱軋,獲得板厚4.0mm之熱軋板。其後,進行1100℃下之退火、及藉由通常之方法之酸洗,之後進行至板厚2.0mm為止之冷軋、900℃下之退火、及利用通常方法之酸洗。 In Table 1 (combining Table 1-1 and Table 1-2 as Table 1), Table 2 (combining Table 2-1 and Table 2-2 as Table 2), and Table 3 (combining Table 3 -1 is combined with Table 3-2 to form the ferritic iron-based stainless steel with the composition shown in Table 3). After melting into a 100 kg steel ingot, it is heated to a temperature of 1200 ° C. Hot rolling was performed to obtain a hot rolled sheet having a thickness of 4.0 mm. Thereafter, annealing at 1100 ° C and pickling by a usual method were performed, followed by cold rolling to a plate thickness of 2.0 mm, annealing at 900 ° C, and pickling by a usual method.
針對所獲得之冷軋退火板,進行孔蝕(pitting corrosion)電位測定(JIS G 0577),而對耐蝕性進行了評價。將孔蝕電位為290mV(vs.SCE)以上者設為「○」(合格)、將未滿290mV者設為「▲」(不合格)而進行了評價。 The obtained cold-rolled annealed sheet was subjected to pitting corrosion potential measurement (JIS G 0577), and the corrosion resistance was evaluated. The evaluation was performed with a pitting potential of 290 mV (vs. SCE) or more as "○" (pass) and a value of less than 290 mV as "▲" (fail).
又,針對所獲得之冷軋退火板,於輥軋方向上採集試片(JIS B 7722 V缺口)而進行夏比衝擊(Charpy impact)試驗,對鋼板之韌性進行評價。將25℃下之夏比衝擊值為200J/cm2以上者設為「○」(合格)、將未滿200J/cm2者設為「▲」(不合格)而進行了評價。 Further, for the obtained cold-rolled annealed sheet, a test piece (JIS B 7722 V notch) was collected in the rolling direction, and a Charpy impact test was performed to evaluate the toughness of the steel sheet. A Charpy impact value at 25 ° C of 200 J / cm 2 or more was evaluated as "○" (Passed), and those below 200 J / cm 2 were evaluated as "▲" (Failed).
進而,藉由對冷軋退火板之表面進行觀察來計測表面之條紋狀圖案之密度,而對表面缺陷之量進行評價。將各組成之鋼板各製作10片,針對各鋼板之正面之中心部之寬度200mm×長度200mm之區域,測定L(長度)方向之長度超過10mm之條紋狀圖案之數量,將其平均數為1以下者設為「○」(合格)、將多於1者設為「▲」(不合格)而進行評價。 Furthermore, by observing the surface of the cold-rolled annealed sheet, the density of the striped pattern on the surface was measured, and the amount of surface defects was evaluated. Ten steel plates of each composition were made, and the number of stripe patterns whose length in the L (length) direction exceeded 10 mm was measured for an area having a width of 200 mm × a length of 200 mm at the central portion of the front surface of each steel plate, and the average number was 1 The following were evaluated as "○" (pass) and more than 1 as "▲" (fail).
進而,使用實施退火之前之冷軋鋼板,對是否即便於880℃下20s之退火中亦會充分地軟質化進行評價。評價係對保持冷軋後之狀態之鋼板之硬度(a)、於880℃下實施20s之退火之鋼板之硬度(b)、及作為於充分地軟質化之情形時之指標而於1000℃實施了20s之退火之鋼板之硬度(c)進行比較而進行評價。於評價中,切割出3片長度15mm×寬度20mm之鋼板,針對測定b及c之試片,於進行上述各種退火後,將鋼板切斷成長度15mm×寬度10mm之尺寸,並使用自該剖面測定出之維氏硬度。若進行退火,則鋼板之硬度自a朝向c而變化,將該軟質化中之90%以上藉 由880℃下20s之退火而達成者,即成為c+0.1×(a-c)≧b者設為「○」(合格)而進行了評價。又,將並非如此者設為「▲」(不合格)而進行了評價。 Furthermore, using the cold-rolled steel sheet before the annealing was performed, it was evaluated whether it was sufficiently softened even in the annealing at 880 ° C. for 20 s. The evaluation is performed on the hardness (a) of the steel sheet maintained in the state after cold rolling, the hardness (b) of the steel sheet annealed at 880 ° C for 20 s, and performed at 1000 ° C as an index when sufficiently softened. The hardness (c) of the annealed steel sheet after 20s was compared and evaluated. In the evaluation, three steel plates with a length of 15 mm × a width of 20 mm were cut, and for the test pieces for measurement b and c, after performing the various annealing described above, the steel plates were cut into a size of 15 mm × 10 mm in width and used from this section. The Vickers hardness was measured. If annealing is performed, the hardness of the steel sheet changes from a to c, and more than 90% of this softening is borrowed. Those who achieved the annealing at 880 ° C for 20 s were evaluated as "○" (pass) if c + 0.1 × (a-c) ≧ b. In addition, the evaluation was performed by setting the case to "▲" (Failure).
將所獲得之結果示於表1、2、3。可知,發明鋼係孔蝕電位測定之評價、夏比衝擊值之評價、表面缺陷之評價、及軟質化溫度之評價全部為「○」,耐蝕性及韌性良好,表面缺陷較少,且於製造性方面亦無問題。 The obtained results are shown in Tables 1, 2, and 3. It can be seen that the evaluation of the pitting corrosion potential measurement, the Charpy impact value evaluation, the surface defect evaluation, and the softening temperature evaluation of the invention steel are all "○". The corrosion resistance and toughness are good, and the surface defects are few. There is no problem with sex.
試驗No.34之比較例係由於Cr含量低於本發明之範圍,故而耐蝕性較差。 The comparative example of test No. 34 was inferior in corrosion resistance because the Cr content was lower than the range of the present invention.
試驗No.35之比較例係由於Cr含量高於本發明之範圍,故而韌性較差。 The comparative example of Test No. 35 is inferior in toughness because the Cr content is higher than the range of the present invention.
試驗No.36之比較例係由於Ni含量低於本發明之範圍,故而耐蝕性較差。 The comparative example of Test No. 36 is inferior in corrosion resistance because the Ni content is lower than the range of the present invention.
試驗No.37之比較例係由於Ti含量低於本發明之範圍,故而耐蝕性較差。 The comparative example of Test No. 37 was inferior in corrosion resistance because the Ti content was lower than the range of the present invention.
試驗No.38之比較例係由於Ti含量高於本發明之範圍,故而韌性較差,且表面缺陷較多。 The comparative example of test No. 38 is because the Ti content is higher than the range of the present invention, the toughness is poor, and there are many surface defects.
試驗No.39之比較例係由於Nb含量低於本發明之範圍,故而韌性較差,且表面缺陷較多。 The comparative example of test No. 39 is because the Nb content is lower than the range of the present invention, the toughness is poor, and there are many surface defects.
試驗No.40之比較例係由於Nb含量高於本發明之範圍,故而軟質化溫度較高,而製造性較差。 The comparative example of test No. 40 is because the Nb content is higher than the range of the present invention, the softening temperature is high, and the manufacturability is poor.
試驗No.41之比較例係由於Zr含量低於本發明之範圍,故而韌性較差,且表面缺陷較多。 The comparative example of test No. 41 is because the Zr content is lower than the range of the present invention, the toughness is poor, and there are many surface defects.
試驗No.42之比較例係由於Zr含量高於本發明之範圍,故而表面缺陷較多。 The comparative example of Test No. 42 has a large number of surface defects because the Zr content is higher than the range of the present invention.
試驗No.57之比較例係由於Nb含量及Zr含量均低於本發明之範圍,故而韌性較差,且表面缺陷較多。 The comparative example of Test No. 57 is because the Nb content and the Zr content are both lower than the range of the present invention, the toughness is poor, and there are many surface defects.
試驗No.58之比較例係由於Ti含量及Zr含量低於本發明之範圍,且Al含量及Nb含量高於本發明之範圍,故而韌性較差且表面缺陷較多,進而軟質化溫度較高而製造性較差。 The comparative example of Test No. 58 is because the Ti content and the Zr content are lower than the range of the present invention, and the Al content and the Nb content are higher than the range of the present invention. Therefore, the toughness is poor and there are many surface defects, and the softening temperature is higher. Poor manufacturability.
再者,針對試驗No.43~54、67、68之比較例,使用圖1及圖2於以下進行說明。 The comparative examples of Test Nos. 43 to 54, 67, and 68 will be described below with reference to FIGS. 1 and 2.
於圖1中,關於本發明例之結果、以及組成為本發明範圍內、滿足Nb≧Zr且不滿足Ti≧Nb之比較例(No.43~48)之結果,針對夏比衝擊值之評價及表面缺陷之評價,於橫軸取Ti含量、且於縱軸取Nb含量而彙總於圖中。再者,圖中所示之鋼板係所有夏比衝擊值之評價合格者其表面缺陷之評價亦合格,夏比衝擊值之結果不合格者其表面缺陷之評價亦不合格。如圖1所示般,為了於本發明之組成範圍內兼顧優異之韌性與表面缺陷之降低,必須滿足Ti≧Nb。 In FIG. 1, the results of the examples of the present invention and the results of the comparative examples (No. 43 to 48) that satisfy Nb ≧ Zr and do not satisfy Ti ≧ Nb within the scope of the present invention are evaluated for the Charpy impact value. And the evaluation of surface defects, the content of Ti is taken on the horizontal axis, and the content of Nb is taken on the vertical axis, and they are summarized in the figure. In addition, the steel plate shown in the figure is all qualified for the evaluation of the surface defects of the Charpy impact value, and those who fail the result of the Charpy impact value are also unqualified for the surface defect. As shown in FIG. 1, in order to balance excellent toughness and reduction of surface defects within the composition range of the present invention, it is necessary to satisfy Ti ≧ Nb.
於圖2中,關於本發明例之結果、以及組成為本發明範圍內、滿足Ti≧Nb且不滿足Nb≧Zr之比較例(No.49~54、67、68)之結果,針對夏比衝擊值之評價及表面缺陷之評價,於橫軸取Nb含量、且於縱軸取Zr含量而彙總於圖中。如圖2所示般,為了於本發明之組成範圍內兼顧優異之韌性與表面缺陷之降低,必須滿足Nb≧Zr。進而,根據圖1及圖2,可知,為了於本發明之組成範圍內兼顧優異之韌性與表面缺陷之降低,必須滿足Ti≧Nb、Nb≧Zr兩者、即滿足Zr≦Nb≦Ti。 In FIG. 2, the results of the examples of the present invention and the results of comparative examples (No. 49 ~ 54, 67, 68) that satisfy Ti ≧ Nb and do not satisfy Nb ≧ Zr within the scope of the present invention are directed to Charpy. The evaluation of the impact value and the evaluation of the surface defect are summarized in the figure by taking the Nb content on the horizontal axis and the Zr content on the vertical axis. As shown in FIG. 2, in order to balance excellent toughness and reduction of surface defects in the composition range of the present invention, it is necessary to satisfy Nb ≧ Zr. Furthermore, according to FIG. 1 and FIG. 2, in order to achieve both excellent toughness and reduction of surface defects within the composition range of the present invention, it is necessary to satisfy both Ti ≧ Nb and Nb ≧ Zr, that is, satisfy Zr ≦ Nb ≦ Ti.
再者,關於試驗No.55及56之比較例,組成係本發明範圍內,且不滿足Ti≧Nb、Nb≧Zr兩者,而夏比衝擊值之結果及表面缺陷之評價兩者皆不合格。 Furthermore, the comparative examples of Test Nos. 55 and 56 are within the scope of the present invention and do not satisfy both Ti ≧ Nb and Nb ≧ Zr. Neither the results of the Charpy impact value nor the evaluation of surface defects. qualified.
本發明之肥粒鐵系不銹鋼板係由於韌性優異、且表面缺陷較少,故而較佳為用作以由升降機之內板代表之室內裝飾、風管罩、排氣管尾喉、儲物櫃、家電製品用零件、商務用品用零件、汽車內裝用零件、汽車排氣用配管、建材、排水溝蓋、海上運輸用集裝箱、器物、廚房設備、建築內外裝材、汽車零件、電扶梯、軌道車輛及電氣裝置殼體外板等為中心之要求耐蝕性之構件,此外可用作要求韌性或設計性之構件。 The ferrous iron-based stainless steel plate of the present invention is preferably used as an interior decoration represented by an inner plate of an elevator, a duct cover, an exhaust pipe tail throat, and a storage cabinet because of its excellent toughness and few surface defects. , Parts for household electrical appliances, parts for business supplies, parts for automobile interiors, pipes for automobile exhausts, building materials, gutter covers, containers for marine transportation, utensils, kitchen equipment, building interior and exterior materials, automobile parts, escalators, Railroad cars and electrical equipment housings are required to have corrosion resistance as the center, and they can also be used as members requiring toughness or design.
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