TWI796838B - Fertilized iron series stainless steel plate - Google Patents
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Abstract
為了提供成形性優異的肥粒鐵系不鏽鋼板，而採用下述肥粒鐵系不鏽鋼板，其是下述成形方法：透過使用衝頭與衝模之壓製成形來將肥粒鐵系不鏽鋼板進行方筒引伸成形至目標成形深度；該肥粒鐵系不鏽鋼板具有下述成分組成：含有：C、Si、Mn、P、S、Cr、N、Al、O、Ti、Nb、Sn、Zr，且該成分組成會滿足下述式(1)及式(2)；並且，板厚為1.0mm以下，圓筒深引伸成形中的臨界引伸比為2.30以上。 (0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0…(1) 0.6×Cr+15×Sn+8×Al≧10.0…(2) In order to provide a ferrous iron-based stainless steel sheet excellent in formability, the following ferrous iron-based stainless steel sheet is adopted, which is a forming method in which a ferrous iron-based stainless steel sheet is squared by press forming using a punch and a die. The barrel is stretched and formed to the target forming depth; the ferrous iron series stainless steel plate has the following composition: containing: C, Si, Mn, P, S, Cr, N, Al, O, Ti, Nb, Sn, Zr, and This component composition satisfies the following formulas (1) and (2); and the plate thickness is 1.0 mm or less, and the critical draw ratio in cylindrical deep drawing forming is 2.30 or more. (0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0…(1) 0.6×Cr+15×Sn+8×Al≧10.0…(2)
Description
發明領域 本發明是有關於肥粒鐵系不鏽鋼板。 field of invention The present invention relates to ferrite-based stainless steel plates.
發明背景 肥粒鐵系不鏽鋼板雖使用在家電製品、廚房機器、電子機器等廣泛領域中，但由於其成形性比沃斯田鐵系不鏽鋼差，故有時用途會受限。惟，近年來，由於精煉技術的提升，使肥粒鐵系不鏽鋼變得能夠極低碳化及極低氮化；還進行了以下嘗試：透過添加Ti、Nb等元素來提高肥粒鐵系不鏽鋼之成形性與耐蝕性。其他還如專利文獻1~3等這般進行了以下嘗試：透過控制成分組成、製造方法來改善肥粒鐵系不鏽鋼之成形性。 Background of the invention Fertilized iron-based stainless steel sheets are used in a wide range of fields such as home appliances, kitchen equipment, and electronic equipment, but their use is sometimes limited because their formability is inferior to that of Worst iron-based stainless steel. However, in recent years, due to the improvement of refining technology, the ferrite-based stainless steel has become extremely low in carbonization and nitrogenation; the following attempts have also been made: to improve the ferrite-based stainless steel by adding Ti, Nb and other elements. formability and corrosion resistance. Others, such as Patent Documents 1 to 3, have attempted to improve the formability of ferritic stainless steel by controlling the composition and manufacturing method.
此等習知改善技術來提升成形性，藉此就能在範圍廣闊之用途中使用肥粒鐵系不鏽鋼；然而，近年來，對於最終製品要求輕量化的情形持續增加，因而不斷要求更進一步的改良。也就是說，在最終製品方面，為了能輕量化，而要求一種板厚比以往還薄且能獲得高成形性的肥粒鐵系不鏽鋼。These conventional improvement techniques improve the formability, so that ferrite-based stainless steel can be used in a wide range of applications; however, in recent years, the demand for lightweight final products has continued to increase, and further improvements have been demanded. improved. That is to say, in order to reduce the weight of the final product, there is a demand for ferrite-based stainless steel with thinner plate thickness than before and high formability.
例如，鼓脹加工是一種如下的加工方法：不使材料流入模具內，而主要是使接觸衝頭之部分拉伸變形的塑性變形來成形。該變形區域會是從衝模肩部到衝頭頭部的區域。在使用模具的方筒成形加工之情況下，一般而言，材料與衝頭之接觸荷重在衝頭肩部附近會最大，而材料的移動會受到拘束，因此，在衝頭肩部與衝模肩部之間，變形會集中而板厚減少會最多。然後，在該部分發生頸縮時會斷裂。For example, bulge processing is a processing method in which a material is not flowed into a mold, but is formed mainly by plastic deformation of a part contacting a punch to be stretched and deformed. This deformed area would be the area from the die shoulder to the punch head. In the case of square tube forming using a die, generally speaking, the contact load between the material and the punch will be the largest near the punch shoulder, and the movement of the material will be restricted. Therefore, between the punch shoulder and the die shoulder Between the parts, the deformation will be concentrated and the plate thickness will be reduced the most. Then, it breaks when necking occurs in that part.
關於該鼓脹成形所成形之構件，就特別需要該構件的用途而言，有家電、廚房的外裝板材(panel)。以往在這種外裝板材上，是使用已對普通鋼施予塗裝的材料，但會有塗裝浮起處、從端部產生生鏽的問題；另一方面，基於不鏽鋼成形性的提升、透過獲得高級感外觀的透明塗裝來提升設計性等理由，近年來多半是將不鏽鋼使用於外裝板材的素材。尤其是，外裝板材會構成製品外觀，故會要求提升尺寸精度。因此，多半會選擇使用鼓脹成形這種加工。As for the member formed by the bulging molding, there are home appliances and kitchen exterior panels (panels) for applications in which the member is particularly required. In the past, this kind of exterior panel has been coated with ordinary steel, but there are problems with the coating floating and rusting from the end; on the other hand, based on the improvement of the formability of stainless steel , In recent years, stainless steel has been mostly used as a material for exterior panels for reasons such as improving design through clear coating for a high-end appearance. In particular, the exterior panel will constitute the appearance of the product, so it is required to improve the dimensional accuracy. Therefore, most of them will choose to use the processing of bulge forming.
又，如上所述，在家電製品、廚房機器等製品中要求輕量化，對於外裝板材也開始強烈要求輕量化。一般認為，該輕量化可透過適當使用下述不鏽鋼來達成，該不鏽鋼之板厚比以往更薄且為0.4mm~小於0.8mm。惟，並不存在一種能在此種板厚下滿足預定鼓脹加工性的肥粒鐵系不鏽鋼板，包含上述專利文獻1~3亦同。Also, as described above, weight reduction is required for products such as home appliances and kitchen appliances, and weight reduction has also begun to be strongly demanded for exterior panels. It is generally believed that this reduction in weight can be achieved through the appropriate use of the following stainless steel whose plate thickness is thinner than before and is 0.4 mm to less than 0.8 mm. However, there is no fat-grained iron-based stainless steel plate that can satisfy the predetermined bulging workability under such a plate thickness, including the above-mentioned patent documents 1 to 3.
專利文獻4記載了一種用於外裝板材的肥粒鐵不鏽鋼板，其具有預定化學成分，板厚為0.4~0.8mm，成形速度為3~10mm/min，並且進行依契遜(Erichsen)試驗時的鼓脹高度達10mm以上。惟，在專利文獻4中，成形速度受限在10mm/min以下，成形品中成形所需時間有一定的限制。於是，要求更進一步提升成形品之生產性。Patent Document 4 describes a fertilized iron stainless steel plate used for exterior panels, which has a predetermined chemical composition, a plate thickness of 0.4~0.8mm, and a forming speed of 3~10mm/min, and is subjected to the Erichsen test When the bulging height reaches 10mm or more. However, in Patent Document 4, the molding speed is limited to 10 mm/min or less, and the time required for molding the molded product is limited to a certain extent. Therefore, it is required to further improve the productivity of molded products.
先前技術文獻 專利文獻 專利文獻1：日本特開昭57-198248號公報 專利文獻2：日本特開昭58-61258號公報 專利文獻3：日本特開2004-217996號公報 專利文獻4：日本特許第6050701號公報 prior art literature patent documents Patent Document 1: Japanese Patent Application Laid-Open No. 57-198248 Patent Document 2: Japanese Patent Application Laid-Open No. 58-61258 Patent Document 3: Japanese Patent Laid-Open No. 2004-217996 Patent Document 4: Japanese Patent No. 6050701
發明概要 發明所欲解決之課題 本發明是有鑑於上述情況而完成者，課題在於提供一種成形性優異的肥粒鐵系不鏽鋼板。 Summary of the invention The problem to be solved by the invention The present invention was made in view of the above circumstances, and it is an object of the present invention to provide a ferrite-based stainless steel plate excellent in formability.
用以解決課題之手段 為了解決上述課題，本發明具有下述構成。 [1]一種肥粒鐵系不鏽鋼板，具有會滿足下述式(1)及式(2)的成分組成，且該成分組成以質量%計含有： C：0.0200%以下、 Si：0.70%以下、 Mn：1.00%以下、 P：0.030%以下、 S：0.005%以下、 Cr：11.0~19.5%、 N：0.020%以下、 Al：0.005~0.100%、 O：0.0050%以下、 Ti：0.03~0.20%、 Nb：0.010~0.300%、 Sn：0.001~0.300%、 Zr：0.001~0.080%， 剩餘部分由鐵及不純物所構成；並且 板厚為1.0mm以下，圓筒深引伸成形中的臨界引伸比為2.30以上； (0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0…(1) 0.6×Cr+15×Sn+8×Al≧10.0…(2) 其中，式(1)及式(2)中的元素符號分別為前述肥粒鐵系不鏽鋼板中各元素的含量(質量%)。 [2]如請求項1之肥粒鐵系不鏽鋼板，其以質量%計含有下述之1種或2種以上來取代Fe之一部分：Mo：0.05~0.50%、Ni：0.05~0.50%、Cu：0.01~1.00%。 [3]如請求項1或請求項2之肥粒鐵系不鏽鋼板，其以質量%計含有下述之1種或2種以上來取代Fe之一部分：B：0.0003~0.0050%、Ga：0.0001~0.2%、W：0.001~0.300%。 [4]如請求項1至請求項3中任一項之肥粒鐵系不鏽鋼板，其平均蘭克福特(Lankford)值為1.8以上，蘭克福特值之面內異向性(Δr)為0.5以上。 means to solve problems In order to solve the above-mentioned problems, the present invention has the following configurations. [1] A ferrite-based stainless steel plate having a composition that satisfies the following formulas (1) and (2), and the composition contains in mass %: C: 0.0200% or less, Si: 0.70% or less, Mn: 1.00% or less, P: less than 0.030%, S: less than 0.005%, Cr: 11.0~19.5%, N: less than 0.020%, Al: 0.005~0.100%, O: less than 0.0050%, Ti: 0.03~0.20%, Nb: 0.010~0.300%, Sn: 0.001~0.300%, Zr: 0.001~0.080%, the remainder consists of iron and impurities; and The plate thickness is less than 1.0mm, and the critical drawing ratio in cylindrical deep drawing forming is more than 2.30; (0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0…(1) 0.6×Cr+15×Sn+8×Al≧10.0…(2) Wherein, the symbols of the elements in formula (1) and formula (2) are the content (mass %) of each element in the aforementioned ferritic stainless steel plate respectively. [2] The ferrite-based stainless steel plate according to claim 1, which contains one or more of the following in place of a part of Fe in mass %: Mo: 0.05~0.50%, Ni: 0.05~0.50%, Cu: 0.01~1.00%. [3] The ferritic iron-based stainless steel plate of claim 1 or claim 2, which contains one or more of the following in place of a part of Fe in mass %: B: 0.0003~0.0050%, Ga: 0.0001 ~0.2%, W: 0.001~0.300%. [4] As for any one of claim 1 to claim 3, the ferritic iron-based stainless steel plate has an average Lankford (Lankford) value of 1.8 or more, and the in-plane anisotropy (Δr) of the Lankford value is 0.5 or more.
發明效果 依照本發明，便可提供一種成形性優異的肥粒鐵系不鏽鋼板。尤其是依照本發明，在製造用以達到家電製品、廚房機器輕量化之零件所需的薄壁成形品時，可使用本發明之肥粒鐵系不鏽鋼板作為胚料且可發揮出良好成形性，故能獲得滿足尺寸精度、設計性的成形品。 Invention effect According to the present invention, there can be provided a ferrite-based stainless steel plate excellent in formability. In particular, according to the present invention, when manufacturing thin-walled molded products required to achieve light weight parts of home appliances and kitchen machines, the ferrite-based stainless steel plate of the present invention can be used as a blank and can exhibit good formability , so molded products satisfying dimensional accuracy and design can be obtained.
本發明的實施形態 用以實施發明之形態 肥粒鐵系不鏽鋼板一般被說是成形性比沃斯田鐵系不鏽鋼板還低，針對該肥粒鐵系不鏽鋼板，為了提升成形性且獲得不生裂紋、成形不良而設計性優異的成形品，本案發明人等進行了精心探討。 Embodiment of the present invention form for carrying out the invention It is generally said that the formability of ferrite-based stainless steel plate is lower than that of Wastian iron-based stainless steel plate. For this ferrite-based stainless steel plate, in order to improve the formability and obtain a formability that is excellent in design without cracking or poor forming products, the inventors of this case conducted careful discussions.
一般而言，成形對象的鋼板其降伏比越低則加工性就越提升。所謂降伏比是降伏應力與抗拉強度的比率；降伏比越低，可獲得均等拉伸之區域的荷重幅度就變得越大，塑性加工會變得越容易進行。另一方面，例如，在圓筒深引伸成形之情況下，成形時鋼板板厚分布會變大，會促使板厚減少，內在的夾雜物會成為起點而變得容易產生裂紋。於是，本案發明人等為了賦予能達到圓筒深引伸成形程度的成形性，調查了肥粒鐵系不鏽鋼所含各元素之種類及含量對成形性之關係。圓筒深引伸成形是一種高難度的成形方式，抑制應力集中部位的板厚減少對於提升成形性很有效。若發生板厚減少，加工性會伴隨加工硬化而降低。詳細觀察成形加工中有產生裂紋之成形品的斷面後，確認到大量的Al氧化物、TiN。認為此等Al氧化物、TiN會促使裂紋，並檢討了能抑制Al氧化物集中存在與抑制TiN成長的鋼成分。於是發現，將具有特定鋼成分之鋼板適用到深引伸成形之胚料，藉此就能使成形滿足尺寸精度。In general, the lower the reduction ratio of the steel sheet to be formed, the more improved the workability is. The so-called yield ratio is the ratio of yield stress to tensile strength; the lower the yield ratio, the greater the load range in the area that can obtain uniform stretching, and the easier it is to perform plastic processing. On the other hand, for example, in the case of cylindrical deep drawing forming, the thickness distribution of the steel plate becomes larger during forming, and the thickness of the steel plate decreases, and internal inclusions become starting points and cracks are likely to occur. Therefore, the inventors of the present invention investigated the relationship between the type and content of each element contained in ferrite-based stainless steel and the formability in order to impart formability to the degree of cylindrical deep drawing forming. Cylindrical deep drawing forming is a difficult forming method, and it is effective to improve the formability by suppressing the thickness reduction of the stress concentration part. If the plate thickness decreases, the workability will decrease with work hardening. A detailed observation of the cross-section of the molded product in which cracks occurred during the forming process revealed a large amount of Al oxide and TiN. These Al oxides and TiN are considered to promote cracks, and steel components that can suppress the concentration of Al oxides and the growth of TiN have been examined. Then, it was found that by applying a steel plate having a specific steel composition to the blank for deep drawing forming, it was possible to make the forming satisfy the dimensional accuracy.
以下，針對本發明實施形態之肥粒鐵系不鏽鋼板進行說明。Hereinafter, the ferrite-based stainless steel plate according to the embodiment of the present invention will be described.
本實施形態之肥粒鐵系不鏽鋼板是如下的鋼板： 其具有會滿足下述式(1)及式(2)的成分組成，且該成分組成以質量%計含有：C：0.0200%以下、Si：0.70%以下、Mn：1.00%以下、P：0.030%以下、S：0.005%以下、Cr：11.0~19.5%、N：0.020%以下、Al：0.005~0.100%、O：0.0050%以下、Ti：0.03~0.20%、Nb：0.010~0.300%、Sn：0.001~0.300%、Zr：0.001~0.080%，剩餘部分由鐵及不純物所構成；並且 板厚為1.0mm以下，圓筒深引伸成形中的臨界引伸比為2.30以上。 (0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0…(1) 0.6×Cr+15×Sn+8×Al≧10.0…(2) 其中，式(1)及式(2)中的元素符號分別為前述肥粒鐵系不鏽鋼板中各元素的含量(質量%)。 再者，肥粒鐵系不鏽鋼板亦可以質量%計含有下述之1種或2種以上來取代Fe之一部分：Mo：0.05~0.50%、Ni：0.05~0.50%、Cu：0.01~1.00%。 更甚者，肥粒鐵系不鏽鋼板亦可以質量%計含有下述之1種或2種以上來取代Fe之一部分：B：0.0003~0.0050%、Ga：0.0001~0.2%、W：0.001~0.300%。 The ferrite-based stainless steel plate of the present embodiment is the following steel plate: It has a component composition that satisfies the following formula (1) and formula (2), and the component composition contains in mass %: C: 0.0200% or less, Si: 0.70% or less, Mn: 1.00% or less, P: 0.030 % below, S: below 0.005%, Cr: 11.0~19.5%, N: below 0.020%, Al: 0.005~0.100%, O: below 0.0050%, Ti: 0.03~0.20%, Nb: 0.010~0.300%, Sn : 0.001~0.300%, Zr: 0.001~0.080%, the remainder is composed of iron and impurities; and The plate thickness is 1.0 mm or less, and the critical draw ratio in cylindrical deep drawing forming is 2.30 or more. (0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0…(1) 0.6×Cr+15×Sn+8×Al≧10.0…(2) Wherein, the symbols of the elements in formula (1) and formula (2) are the content (mass %) of each element in the aforementioned ferritic stainless steel plate respectively. Furthermore, the ferrite-based stainless steel plate may contain one or more of the following in mass % instead of a part of Fe: Mo: 0.05~0.50%, Ni: 0.05~0.50%, Cu: 0.01~1.00% . What's more, the ferrite-based stainless steel plate can also contain one or more of the following in mass % instead of a part of Fe: B: 0.0003~0.0050%, Ga: 0.0001~0.2%, W: 0.001~0.300 %.
說明肥粒鐵系不鏽鋼板之化學成分的限定理由。另外，只要沒有特別註記，成分含量之單位即%意指：質量%。The reasons for limiting the chemical composition of ferritic stainless steel sheets will be explained. In addition, as long as there is no special note, %, which is the unit of component content, means: mass %.
C：0.0200%以下 C基於會使成形性與耐蝕性劣化之理由，其含量越少越好，上限設為0.0200%以下。惟，過度減低C量會牽連到精煉成本增加，故C量之下限宜設為0.0010%以上。適宜的C量為0.0030~0.0070%。 C: 0.0200% or less Since C degrades the formability and corrosion resistance, the less the content, the better, and the upper limit is 0.0200% or less. However, excessively reducing the amount of C will involve an increase in refining costs, so the lower limit of the amount of C should be set above 0.0010%. The appropriate amount of C is 0.0030~0.0070%.
Si：0.70%以下 Si有時雖會作為脫氧元素來含有，但其為固溶強化元素，因此從降低降伏應力之觀點來看，其含量越少越好，上限設為0.70%以下。但是，過度減低Si量會牽連到精煉成本增加，故下限宜設為0.01%以上。適宜的Si量為0.05~0.50%。 Si: less than 0.70% Si is sometimes contained as a deoxidizing element, but it is a solid-solution strengthening element, so from the viewpoint of reducing the yield stress, the less the content, the better, and the upper limit is made 0.70% or less. However, excessively reducing the amount of Si leads to an increase in refining costs, so the lower limit is preferably set to 0.01% or more. The suitable amount of Si is 0.05~0.50%.
Mn：1.00%以下 Mn與Si同樣是固溶強化元素，因此從降低降伏應力之觀點來看，其含量越少越好，上限設為1.00%以下。但是，過度減低Mn量會牽連到精煉成本增加，故下限宜設為0.01%以上。適宜的Mn量為0.05~0.50%。 Mn: less than 1.00% Like Si, Mn is a solid-solution strengthening element, so from the viewpoint of reducing the yield stress, the less the content, the better, and the upper limit is made 1.00% or less. However, excessively reducing the amount of Mn leads to an increase in refining costs, so the lower limit is preferably set to 0.01% or more. The suitable amount of Mn is 0.05~0.50%.
P：0.030%以下 P是不可避免會從原料混進來的元素，其還與Si、Mn同樣是固溶強化元素，故其含量越少越好，從拉伸之觀點來看，上限設為0.030%以下。宜小於0.030%，較宜為0.025%以下。但是，過度減低P量會牽連到精煉成本增加，故下限亦可設為0.010%以上。 P: less than 0.030% P is an element inevitably mixed in from raw materials, and it is also a solid-solution strengthening element like Si and Mn, so its content should be as small as possible. From the viewpoint of elongation, the upper limit is 0.030% or less. It should be less than 0.030%, preferably less than 0.025%. However, excessively reducing the amount of P will lead to an increase in refining costs, so the lower limit may be set to 0.010% or more.
S：0.005%以下 S在Ti添加鋼之情況下會與Ti、C一起形成Ti 4C 2S 2，而具有使C固定化之作用。Ti 4C 2S 2是一種在高溫下析出的粗大析出物，故對於再結晶、粒成長現象的影響少，不過，若大量析出該析出物，會變成生鏽起點而耐蝕性會劣化。因此，S之上限設為0.005%以下。但是，過度減低S量會牽連到精煉成本增加，故S量之下限亦可設為0.0001%以上。 S: less than 0.005% S will form Ti 4 C 2 S 2 together with Ti and C when Ti is added to the steel, and has the function of immobilizing C. Ti 4 C 2 S 2 is a coarse precipitate that precipitates at high temperature, so it has little influence on recrystallization and grain growth phenomena. However, if a large amount of this precipitate is precipitated, it will become a starting point of rust and the corrosion resistance will deteriorate. Therefore, the upper limit of S is made 0.005% or less. However, excessively reducing the amount of S will involve an increase in refining costs, so the lower limit of the amount of S can also be set at 0.0001% or more.
Cr：11.0~19.5% 關於Cr，為了提升耐蝕性就必須含有11.0%以上，但過量含有會使韌性劣化，除了製造性變差之外，也會使降伏應力增高。因此，Cr之上限設為19.5%以下。適宜的Cr量為13.0~17.5%。 Cr: 11.0~19.5% Concerning Cr, it is necessary to contain 11.0% or more in order to improve the corrosion resistance, but excessive content will deteriorate the toughness and not only deteriorate the manufacturability, but also increase the yield stress. Therefore, the upper limit of Cr is made 19.5% or less. The appropriate amount of Cr is 13.0~17.5%.
N：0.020%以下 N與C同樣會使成形性與耐蝕性劣化，故其含量越少越好，上限設為0.020%以下。但是，從減量所耗費之製造成本的觀點來看，下限亦可設為0.003%以上。適宜的N量為0.005~0.015%。 N: less than 0.020% N and C also degrade the formability and corrosion resistance, so the less the content, the better, and the upper limit is 0.020% or less. However, the lower limit may be set to 0.003% or more from the viewpoint of manufacturing costs for weight reduction. The suitable amount of N is 0.005~0.015%.
Al：0.005~0.100% Al亦可作為脫氧元素而含有0.005%以上。另一方面，過度含有Al會使成形性、熔接性降低，還恐會導致表面品質劣化，故上限設為0.100%以下。適宜的Al量為0.010~0.080%。 Al: 0.005~0.100% Al may be contained in an amount of 0.005% or more as a deoxidizing element. On the other hand, excessive Al content may lower formability and weldability, and may cause deterioration of surface quality, so the upper limit is made 0.100% or less. The suitable amount of Al is 0.010~0.080%.
O：0.0050%以下 O會使耐蝕性及加工性降低。因此，O量必須壓低，上限設為0.0050%以下。惟，過度減低O量會使精煉成本提高，O量之下限亦可設為0.0001%以上。O量適宜的範圍為0.0005~0.0030%。 O: less than 0.0050% O lowers corrosion resistance and workability. Therefore, the amount of O must be kept low, and the upper limit is made 0.0050% or less. However, excessively reducing the amount of O will increase the refining cost, and the lower limit of the amount of O can also be set above 0.0001%. The suitable range of O content is 0.0005~0.0030%.
Ti：0.03~0.20% Ti會與C、N、S結合形成夾雜物，其具有提升耐蝕性、耐晶界腐蝕性及深引伸性之效果，故含有0.03%以上。另一方面，Ti由於是固溶強化元素，故過度含有Ti會牽連到固溶Ti增加，而牽連到鼓脹性指標即拉伸率降低。於是，Ti之上限設為0.20%以下。適宜的Ti量為0.08~0.12%。 Ti: 0.03~0.20% Ti will combine with C, N, and S to form inclusions, which have the effect of improving corrosion resistance, intergranular corrosion resistance, and deep drawability, so it contains more than 0.03%. On the other hand, since Ti is a solid-solution strengthening element, excessive Ti content leads to an increase in solid-solution Ti, which leads to a decrease in elongation, which is a swellability index. Therefore, the upper limit of Ti is made 0.20% or less. The suitable amount of Ti is 0.08~0.12%.
Nb：0.010~0.300% Nb是會提升成形性與耐蝕性的元素，透過含有0.010%以上會展現其效果。但是，過度含有會導致固溶強化致使延展性降低，故設為0.300%以下。適宜的Nb量為0.100~0.200%。 Nb: 0.010~0.300% Nb is an element that improves formability and corrosion resistance, and its effect will be exhibited by containing 0.010% or more. However, excessive content causes solid-solution strengthening to lower ductility, so it is made 0.300% or less. The appropriate amount of Nb is 0.100~0.200%.
Sn：0.001~0.300% 關於Sn，含有時會具有使降伏比降低而提升鼓脹加工性之效果。為了獲得此效果，含有Sn為0.001%以上。另一方面，過量含有時製造性會劣化，故上限設為0.300%以下。適宜的Sn量為0.020~0.200%。 Sn: 0.001~0.300% Concerning Sn, when contained, it has the effect of reducing the yield ratio and improving the swelling workability. In order to obtain this effect, Sn is contained at 0.001% or more. On the other hand, if it is contained in excess, the manufacturability will deteriorate, so the upper limit is made 0.300% or less. The suitable amount of Sn is 0.020~0.200%.
Zr：0.001~0.080% Zr是作為脫氧元素而含有0.001%以上。另一方面，過度含有Zr會導致成形性、熔接性及表面品質劣化，故上限設為0.080%以下。適宜的Zr量為0.002~0.020%。 Zr: 0.001~0.080% Zr is contained as a deoxidizing element at 0.001% or more. On the other hand, excessive Zr content will degrade formability, weldability, and surface quality, so the upper limit is made 0.080% or less. The suitable amount of Zr is 0.002~0.020%.
(0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0 詳細觀察有產生裂紋之成形品的斷面時，可觀察到Al氧化物與塊狀TiN，所述Al氧化物存在於大多數的凹坑(dimple)底部，塊狀TiN則無關乎凹坑而存在，其等會成為裂紋起點或促使龜裂傳播。為了抑制Al氧化物集中存在與抑制TiN成長，有效的是夾雜物組成之改質，活用強脫氧劑即Zr很有效。嚴密調查Al、Ti、O及Zr之含量與產生裂紋之關係後，結果發現，(0.4×Al+0.5×Zr+0.1×Ti)/O達12.0以上時，會顯示出優異的成形性。因此，本實施形態之肥粒鐵系不鏽鋼板宜滿足(0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0。 (0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0 When the cross-section of a molded product with cracks is observed in detail, Al oxide and bulk TiN can be observed. The Al oxide exists at the bottom of most dimples, and the bulk TiN is not related to the dimple. Existence, etc. will become the origin of cracks or promote crack propagation. In order to suppress the concentration of Al oxides and the growth of TiN, it is effective to modify the composition of inclusions, and it is effective to use Zr, which is a strong deoxidizer. After closely investigating the relationship between the content of Al, Ti, O, and Zr and the occurrence of cracks, it was found that when (0.4×Al+0.5×Zr+0.1×Ti)/O exceeds 12.0, it will show excellent formability. Therefore, the ferrite-based stainless steel plate of this embodiment preferably satisfies (0.4×Al+0.5×Zr+0.1×Ti)/O≧12.0.
0.6×Cr+15×Sn+8×Al≧10.0 為了提升圓筒深引伸成形性，就必須抑制皺褶與抑制加工末期板厚增加；所述抑制皺褶是抑制凸緣的皺褶同時使材料流入。肥粒鐵系不鏽鋼由於斷裂強度不高而無法提高防皺按壓力，因而透過高潤滑化的對策就會變得很有效。為了達到高潤滑化，雖然一般會使用潤滑劑，但在成形之加工末期中，材料與模具之面壓非常高，導致潤滑劑被排了出來。在潤滑劑效果會變弱的加工條件下，材料之表面皮膜、濃度分布的影響就會變得顯著。於不鏽鋼雖存在有鈍態皮膜，但在製造步驟中生成的氧化物、發生朝表面層變濃等現象，而存在有各種各樣的元素濃度分布。就形成鈍態皮膜而言，Cr雖是不可欠缺的元素，但由於模具、模具塗層(coating)多半會含有Cr，故透過此組合，會因為親和力而誘發模具刮傷。於是，透過使該鈍態皮膜中存在有會形成強固氧化物的Al，藉此抑制模具刮傷而確保穩定的成形性。又，Sn容易存在於表面，且其相較於其他元素是較為軟質，故會發揮出緩和應力集中之效果。經嚴密調查Cr、Al及Sn之含量與臨界引伸比的關係後，結果發現，0.6×Cr+15×Sn+8×Al達10.0以上時，臨界引伸比會穩定且大於2.30。因此，本實施形態之肥粒鐵系不鏽鋼板宜滿足0.6×Cr+15×Sn+8×Al≧10.0。 0.6×Cr+15×Sn+8×Al≧10.0 In order to improve the deep-drawing formability of the cylinder, it is necessary to suppress the wrinkle and the increase of the plate thickness at the end of processing; the wrinkle suppression is to suppress the wrinkle of the flange while allowing the material to flow in. Fertilized iron-based stainless steel cannot increase the anti-wrinkle pressing force due to its low fracture strength, so the countermeasures through high lubrication will become very effective. In order to achieve high lubrication, lubricants are generally used, but at the end of the forming process, the surface pressure between the material and the mold is very high, causing the lubricant to be discharged. Under the processing conditions where the effect of the lubricant is weakened, the influence of the surface film of the material and the concentration distribution will become significant. Although there is a passive film on stainless steel, the oxides formed during the manufacturing process become concentrated toward the surface layer, and there are various element concentration distributions. Although Cr is an indispensable element for forming a passive film, since most molds and mold coatings contain Cr, through this combination, mold scratches will be induced due to affinity. Therefore, by making Al which forms a strong oxide exist in this passivation film, the mold scratch is suppressed and stable formability is ensured. In addition, Sn is easy to exist on the surface, and it is softer than other elements, so it exerts the effect of alleviating stress concentration. After a close investigation of the relationship between the content of Cr, Al and Sn and the critical drawing ratio, it was found that when 0.6×Cr+15×Sn+8×Al reaches more than 10.0, the critical drawing ratio will be stable and greater than 2.30. Therefore, the ferrite-based stainless steel plate of this embodiment preferably satisfies 0.6×Cr+15×Sn+8×Al≧10.0.
又，本實施形態之肥粒鐵系不鏽鋼板以質量%計亦可含有下述之1種或2種以上來取代Fe之一部分：Mo：0.05~0.50%、Ni：0.05~0.50%、Cu：0.01~1.00%。In addition, the ferrite-based stainless steel plate of this embodiment may also contain one or more of the following to replace part of Fe in mass %: Mo: 0.05-0.50%, Ni: 0.05-0.50%, Cu: 0.01~1.00%.
Mo、Ni、Cu是一種會提升耐蝕性之元素，在要求耐蝕性之用途中視需要而含有1種或2種以上即可。Mo、Ni分別含有0.05%以上，藉此會提升耐蝕性。過度含有Mo、Ni會招致硬質化，並導致成形性劣化，故分別定0.50%以下為上限。適宜的Mo量及Ni量分別為0.10~0.30%。又，Cu含有0.01%以上會展現其效果，但過度含有Cu會導致成形性劣化，尤其是延展性劣化，故Cu量之上限設為1.00%以下。適宜的Cu量為0.30~0.80%。Mo, Ni, and Cu are elements that improve corrosion resistance, and one or more of them may be contained as necessary for applications requiring corrosion resistance. When Mo and Ni are respectively contained in an amount of 0.05% or more, the corrosion resistance is improved. Excessive content of Mo and Ni will cause hardening and deterioration of formability, so 0.50% or less of each is set as the upper limit. The suitable Mo amount and Ni amount are 0.10~0.30% respectively. Moreover, Cu contains 0.01% or more to exhibit its effect, but excessive Cu content will lead to deterioration of formability, especially ductility deterioration, so the upper limit of Cu amount is made 1.00% or less. The suitable amount of Cu is 0.30~0.80%.
又，本實施形態之肥粒鐵系不鏽鋼板亦可以質量%計含有下述之1種或2種以上來取代Fe之一部分：B：0.0003~0.0050%、Ga：0.0001~0.2%、W：0.001~0.300%。In addition, the ferrite-based stainless steel plate of this embodiment may contain one or more of the following in mass % instead of a part of Fe: B: 0.0003-0.0050%, Ga: 0.0001-0.2%, W: 0.001 ~0.300%.
B是一種會提升二次加工性之元素，視需要亦可含有B為0.0003%以上。惟，過度含有B會導致拉伸率降低，故含有B時之上限設為0.0050%以下。適宜的B量為0.0010~0.0020%。B is an element that improves the secondary processability, and B can be contained at 0.0003% or more if necessary. However, excessive inclusion of B leads to a reduction in elongation, so the upper limit of the inclusion of B is made 0.0050% or less. The suitable amount of B is 0.0010~0.0020%.
Ga是一種會形成GaS而提升耐蝕性之元素。透過抑制MnS析出可消除生鏽起點，故其是一種非常有效的元素。含有小於0.0001%時無法確認效果，故含有Ga時亦可含有0.0001%以上。另一方面，過量含有Ga會招致固溶硬化。據此，Ga量之上限設為0.2%以下。Ga is an element that forms GaS to improve corrosion resistance. It is a very effective element because it eliminates the origin of rust by inhibiting the precipitation of MnS. If the content is less than 0.0001%, the effect cannot be confirmed, so when Ga is contained, 0.0001% or more may be contained. On the other hand, excessive Ga content causes solution hardening. Accordingly, the upper limit of the amount of Ga is made 0.2% or less.
W與Nb、Ti同樣會固定C、N而防止Cr碳氮化物所致之敏化(sensitization)，其是一種會提升耐蝕性之元素。若要展現出此種效果，W量設為0.001%以上即可。另一方面，W量大於0.300%時會招致不鏽鋼板之硬質化而降低加工性。據此，W量宜設為0.300%以下。W, like Nb and Ti, fixes C and N to prevent sensitization caused by Cr carbonitrides, and is an element that improves corrosion resistance. To exhibit this effect, the amount of W should be set to 0.001% or more. On the other hand, if the amount of W exceeds 0.300%, the stainless steel plate will be hardened and the workability will be reduced. Accordingly, the amount of W is preferably set to 0.300% or less.
關於本實施形態之肥粒鐵系不鏽鋼板，其除了上述元素以外，是由Fe及不純物(不純物也包含不可避免的不純物)所構成。又，在不損及本發明效果之範圍下，亦可含有以上說明的各元素之外的元素。在本實施形態中雖可含有例如Bi、Pb、Se、H等，但此時宜盡可能降低。另一方面，此等元素在可解決本發明課題之限度下，其含有比例受到控制，並因應需要亦可含有：Bi為0.01%以下，Pb為0.01%以下，Se為0.01%以下，H為0.01%以下。The ferrite-based stainless steel plate of this embodiment is composed of Fe and impurities (impurities also include unavoidable impurities) in addition to the above-mentioned elements. In addition, elements other than the respective elements described above may be contained within a range that does not impair the effects of the present invention. In this embodiment, for example, Bi, Pb, Se, H, etc. may be contained, but in this case it is preferable to reduce it as much as possible. On the other hand, the content ratio of these elements is controlled to the extent that the subject of the present invention can be solved, and may also contain as required: Bi is 0.01% or less, Pb is 0.01% or less, Se is 0.01% or less, and H is 0.01% or less. Below 0.01%.
在本實施形態之成形方法中，是以板厚1.0mm以下之肥粒鐵系不鏽鋼板作為成形對象。適宜的板厚為0.4~0.8mm。本實施形態之肥粒鐵系不鏽鋼板透過調整化學成分而鼓脹性優異，故特別適合使用在家電製品、廚房機器這種必須以薄板厚進行成形加工的用途中。In the forming method of this embodiment, ferrite-based stainless steel plates with a plate thickness of 1.0 mm or less are used as forming objects. The suitable plate thickness is 0.4~0.8mm. The ferrite-based stainless steel plate of this embodiment has excellent swellability by adjusting the chemical composition, so it is especially suitable for use in applications such as home appliances and kitchen machines that must be formed with a thin plate thickness.
圓筒深引伸成形中的臨界引伸比：2.30以上 為了在圓筒深引伸成形中提高臨界引伸比，就必須使用相對成形品之徑還要大的胚料徑。肥粒鐵系不鏽鋼雖具有適合引伸成形之高r值，但另一方面其斷裂強度低，一旦來自凸緣的流入堵塞時，在側壁就會產生裂紋。為了促使材料從凸緣流入，雖可適當使用高潤滑條件，但在胚料徑大之情況下，由於在凸緣部的接觸長度會變長，因而在加工末期容易發生潤滑耗盡。在本案中是限定了成分範圍，該成分範圍即使在加工末期之潤滑耗盡也能獲得效果，並且臨界引伸比為2.30以上，其效果會變得明確。 Critical drawing ratio in cylindrical deep drawing forming: 2.30 or more In order to increase the critical drawing ratio in cylindrical deep drawing forming, it is necessary to use a blank material diameter larger than the diameter of the formed product. Ferrous iron-based stainless steel has a high r-value suitable for drawing forming, but on the other hand, its fracture strength is low, and if the inflow from the flange is blocked, cracks will occur on the side wall. In order to promote the flow of material from the flange, high lubrication conditions can be used appropriately, but in the case of a large billet diameter, since the contact length at the flange portion will become longer, lubrication exhaustion will easily occur at the end of processing. In this case, the composition range is limited, and the effect can be obtained even if the lubrication is exhausted at the end of processing, and the critical draw ratio is 2.30 or more, and the effect will become clear.
圓筒深引伸成形中的臨界引伸比是依以下順序來進行測定。準備板厚0.8mm且具有各種直徑之圓形胚材，對於各胚料施行圓筒深引伸成形；圓筒深引伸成形是使用下述形狀的模具：Die：內徑43mm，Die r4mm，Punch：直徑40mm。防皺按壓壓力是設為10kN。然後，求出在不斷裂下可成形的胚料最大直徑Dmax，並將Dmax與衝頭之直徑d的比(Dmax/d)定為臨界引伸比。The critical draw ratio in cylindrical deep drawing forming was measured in the following procedure. Prepare circular blanks with a plate thickness of 0.8mm and various diameters, and perform cylindrical deep drawing forming on each blank; cylindrical deep drawing forming uses a mold with the following shape: Die: inner diameter 43mm, Die r4mm, Punch: 40mm in diameter. The anti-wrinkle pressing pressure is set to 10kN. Then, the maximum diameter Dmax of the blank that can be formed without breaking is obtained, and the ratio (Dmax/d) of Dmax to the diameter d of the punch is determined as the critical drawing ratio.
又，本實施形態之肥粒鐵系不鏽鋼板其平均蘭克福特值(以下記載為平均r值；亦稱為平均塑性應變比)為1.8以上，且其蘭克福特值之面內異向性(Δr)為0.5以上，或宜大於0.7。平均r值設為1.8以上，藉此在使用衝頭與衝模之成形中，在衝頭肩部不易發生板厚減少，以及在凸緣部對於寬度縮減變形之阻抗會減少，就能抑制成形加工時產生裂紋。又，面內異向性(Δr)設為0.5以上，藉此在成形時之凸緣變形中，面內異向性會變大，並於凸緣部之板厚會產生差值，從而會存在能確保潤滑劑之區域，因而能更為提升成形性。In addition, the average Lankford value (hereinafter referred to as the average r value; also referred to as the average plastic strain ratio) of the ferrite-based stainless steel plate of this embodiment is 1.8 or more, and the in-plane anisotropy of the Lankford value is (Δr) is at least 0.5, or preferably greater than 0.7. The average r value is set to 1.8 or more, so that in the forming using a punch and a die, the plate thickness reduction is less likely to occur at the punch shoulder, and the resistance to the width reduction deformation of the flange is reduced, and the forming process can be suppressed. When cracks occur. In addition, if the in-plane anisotropy (Δr) is set to 0.5 or more, the in-plane anisotropy will increase during the deformation of the flange during forming, and a difference will occur in the thickness of the flange portion, resulting in There is a region where lubricant can be ensured, so the formability can be further improved.
平均r值及Δr之測定方法可透過JIS Z 2254：2008之塑性應變比試驗方法來求得。平均r值可根據JIS Z 2254：2008並透過下述式(A)來求得。又，面內異向性(Δr)可依據JIS Z 2254：2008並透過下述式(B)來求得。The average r value and Δr can be measured by the plastic strain ratio test method of JIS Z 2254:2008. The average r value can be obtained by the following formula (A) according to JIS Z 2254:2008. In addition, the in-plane anisotropy (Δr) can be obtained by the following formula (B) in accordance with JIS Z 2254:2008.
平均r值＝(r 0+2r 45+r 90)/4・・・(A) Average r value = (r 0 +2r 45 +r 90 )/4・・・(A)
Δr＝(r 0-2r 45+r 90)/2・・・(B) Δr＝(r 0 -2r 45 +r 90 )/2・・・(B)
其中，(A)式及(B)式中的r 0表示輥軋方向之r值，r 90表示與輥軋呈垂直方向之r值，r 45表示與輥軋呈45度方向之r值。 Among them, r 0 in formulas (A) and (B) represents the r value in the rolling direction, r 90 represents the r value in the direction perpendicular to the rolling, and r 45 represents the r value in the direction 45 degrees to the rolling.
本實施形態之肥粒鐵系不鏽鋼板可透過一般的方法來製造，並無特別限定。亦即，以製鋼及連續鑄造來鑄造出具有所欲化學成分之鑄片，並施行熱輥軋、熱輥軋後的退火及酸洗、冷輥軋及冷輥軋後的最終退火，藉此來進行製造即可。但是，為了提高臨界引伸比同時使平均r值及面內異向性(Δr)在適宜範圍，冷輥軋率宜設在78~94%之範圍，冷輥軋後之最終退火的昇溫速度宜設為大於20℃/秒之範圍且宜設為200℃/秒以下，最終退火之均熱速度及均熱時間宜分別設為830~950℃、30秒以上且2分以下之範圍，從均熱結束後起至500℃為止之冷卻速度宜設為15~30℃/秒之範圍。The ferrite-based stainless steel plate of this embodiment can be manufactured by a general method, and is not particularly limited. That is, steelmaking and continuous casting are used to cast cast slabs with the desired chemical composition, and hot rolling, annealing and pickling after hot rolling, cold rolling and final annealing after cold rolling are performed, thereby to manufacture. However, in order to increase the critical elongation ratio and keep the average r value and in-plane anisotropy (Δr) in the appropriate range, the cold rolling ratio should be set in the range of 78~94%, and the temperature rise rate of the final annealing after cold rolling should be Set it to a range greater than 20°C/s and should be set below 200°C/s. The soaking speed and soaking time of the final annealing should be set to 830~950°C, 30 seconds or more and 2 minutes or less, respectively. The cooling rate from the end of heating to 500°C should be set in the range of 15~30°C/sec.
若對於具有本實施形態化學成分的不鏽鋼施行最終退火，則在最終退火時，鋼中的P會微細析出變成P析出物，這恐怕會在再結晶時讓混合晶粒組織形成出來而對成形性帶來不良影響。惟，透過施行上述冷輥軋及最終退火，圓筒深引伸成形中的臨界引伸比會達2.30以上，進一步還將平均蘭克福特值作成1.8以上，蘭克福特值之面內異向性(Δr)會達0.5以上。藉此，就能獲得一種成形性優異的肥粒鐵系不鏽鋼板。 [實施例] If final annealing is performed on stainless steel having the chemical composition of the present embodiment, during final annealing, P in the steel will be finely precipitated and become P precipitates, which may cause a mixed grain structure to form during recrystallization and affect the formability. bring adverse effects. However, through the above-mentioned cold rolling and final annealing, the critical drawing ratio in the deep drawing of the cylinder will reach more than 2.30, and the average Lankford value will be made more than 1.8, and the in-plane anisotropy of the Lankford value ( Δr) will be more than 0.5. Thereby, a ferrite-based stainless steel plate having excellent formability can be obtained. [Example]
以下，透過實施例而更為詳細說明本發明。 將表1A及表1B所示成分組成之肥粒鐵系不鏽鋼予以熔煉、鑄造，再以熱輥軋作成厚度5.0mm的熱軋板。另外，在表1A及表1B所示成分組成中，剩餘部分為Fe及不純物。之後，施行熱軋板退火並進行酸洗後，進行冷輥軋至厚度0.3~1.2mm，並施行退火、酸洗，之後施予調質輥軋而作成表2所示之鋼板。 Hereinafter, the present invention will be described in more detail through examples. Fertilized iron-based stainless steel with the composition shown in Table 1A and Table 1B was smelted, cast, and then hot-rolled to make a hot-rolled plate with a thickness of 5.0mm. In addition, in the composition shown in Table 1A and Table 1B, the remainder is Fe and impurities. After that, the hot-rolled sheet was annealed and pickled, then cold-rolled to a thickness of 0.3 to 1.2 mm, annealed and pickled, and then tempered and rolled to produce the steel sheets shown in Table 2.
另外，關於No.1~33之鋼板，是將冷輥軋率設為如表2所記載者，並將冷輥軋後之最終退火的昇溫速度設為大於20℃/秒之範圍，最終退火之均熱速度及均熱時間分別設為830~950℃、30秒~2分之範圍，從均熱結束後起至500℃為止之冷卻速度設為15~30℃/秒之範圍。使用此方式所得之鋼板，進行圓筒深引伸成形試驗。In addition, regarding the steel sheets No. 1 to 33, the cold rolling rate was set as described in Table 2, and the temperature increase rate of the final annealing after cold rolling was set to be greater than 20°C/sec. The soaking speed and soaking time are set in the range of 830~950°C and 30 seconds~2 minutes respectively, and the cooling rate from the end of soaking to 500°C is set in the range of 15~30°C/sec. Using the steel plate obtained in this way, the cylindrical deep drawing forming test was carried out.
成形試驗是使用Erichsen公司製之145-60型成形試驗機。將鋼板切成圓板狀作為胚料。胚料之尺寸設為φ84~94mm，並使用下述形狀的模具：Die：內徑43mm，Die r4mm，Punch：直徑40mm。防皺按壓壓力設為10kN。以Johnson Wax ＃122作為潤滑劑而輕輕地施加在成形加工面。維持該成形條件，並將衝頭相對衝模的成形速度設為20mm/min而進行成形試驗。另外，透過無凸緣殘留的引伸沖裁成形來看是否產生裂紋，藉此判定可否成形。For the forming test, a 145-60 forming test machine manufactured by Erichsen Co., Ltd. was used. Cut the steel plate into a disc shape as a blank. The size of the billet is set to φ84~94mm, and the following molds are used: Die: inner diameter 43mm, Die r4mm, Punch: diameter 40mm. The anti-wrinkle pressing pressure is set to 10kN. Apply Johnson Wax #122 as a lubricant to the forming surface lightly. The forming conditions were maintained, and a forming test was performed by setting the forming speed of the punch relative to the die at 20 mm/min. In addition, whether or not cracks occur is judged by stretch punching without flange remaining, and it is judged whether forming is possible.
關於成形後之成形品，有產生裂紋、形狀不良者評價為NG，未產生裂紋、形狀不良者評價為OK。結果列示於表2。Regarding the molded product after molding, those with cracks and poor shape were rated as NG, and those without cracks and poor shape were rated as OK. The results are listed in Table 2.
關於鋼板之0.2%偏位降伏強度、拉伸率之測定，是使用JIS13號B試驗片，並依據JIS Z 2241所記載之條件，並從平行於輥軋方向的0°方向來取樣實施。進一步地，關於平均r值及Δr，則是從試驗片取樣方向相對輥軋方向為0°、45°、90°方向進行取樣而獲得樣品，從所述樣品以賦予16%應變之條件來進行測定。The measurement of the 0.2% deflection yield strength and elongation of the steel plate is to use the JIS13 No. B test piece, and according to the conditions described in JIS Z 2241, and take samples from the 0° direction parallel to the rolling direction. Furthermore, regarding the average r value and Δr, the samples were obtained by sampling from the direction of the test piece sampling direction at 0°, 45°, and 90° relative to the rolling direction, and the samples were obtained under the condition of imparting a strain of 16%. Determination.
圓筒深引伸成形中的臨界引伸比則是依以下順序來測定。準備板厚0.8mm且具有各種直徑的圓形胚材，對於各胚料施行圓筒深引伸成形，圓筒深引伸成形是使用下述形狀的模具：Die：內徑43mm，Die r4mm，Punch：直徑40mm。防皺按壓壓力設為10kN。然後，求出在不斷裂下可成形的胚料最大直徑Dmax，並將Dmax與衝頭之直徑d的比(Dmax/d)定為臨界引伸比。The critical draw ratio in cylindrical deep draw forming is measured in the following procedure. Prepare circular blanks with a plate thickness of 0.8mm and various diameters, and perform cylindrical deep drawing forming on each blank. The cylindrical deep drawing forming uses a mold with the following shape: Die: inner diameter 43mm, Die r4mm, Punch: 40mm in diameter. The anti-wrinkle pressing pressure is set to 10kN. Then, the maximum diameter Dmax of the blank that can be formed without breaking is obtained, and the ratio (Dmax/d) of Dmax to the diameter d of the punch is determined as the critical drawing ratio.
如表1A、表1B及表2所示，以本發明範圍內的條件進行成形者，於成形品並未產生裂紋、形狀不良，而且成形品之設計性亦良好。As shown in Table 1A, Table 1B, and Table 2, those molded under the conditions within the range of the present invention did not cause cracks or defects in the molded product, and the design of the molded product was also good.
另一方面，以本發明範圍外的條件進行成形者，於成形品產生了裂紋、形狀不良。On the other hand, when molding was performed under conditions outside the scope of the present invention, cracks and shape defects occurred in the molded product.
[表1A]
[表1B]
[表2]
產業上之可利用性 本發明可提供一種成形性優異的肥粒鐵系不鏽鋼板，於此點上具有產業上的可利用性。尤其是依照本發明，在製造用以達成家電製品、廚房機器輕量化之零件所需的薄壁成形品時，可使用本發明之肥粒鐵系不鏽鋼板作為胚料且可發揮出良好成形性，故能獲得滿足尺寸精度、設計性的成形品，於此點上具有產業上的可利用性。 Industrial availability The present invention can provide a ferrite-based stainless steel plate excellent in formability, and has industrial applicability in this point. In particular, according to the present invention, when manufacturing thin-walled molded products required to achieve light weight parts of home appliances and kitchen machines, the ferrite-based stainless steel plate of the present invention can be used as a blank and can exhibit good formability , so molded products satisfying dimensional accuracy and designability can be obtained, which has industrial applicability in this point.
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| CN101437974A (en) * | 2006-05-09 | 2009-05-20 | 新日铁住金不锈钢株式会社 | Stainless steel excellent in corrosion resistance, ferritic stainless steel excellent in resistance to crevice corrosion and formability, and ferritic stainless steel excellent inresistance to crevice |
| TW201435098A (en) * | 2013-02-04 | 2014-09-16 | Nippon Steel & Sumikin Sst | Ferritic stainless steel sheet with excellent workability and process for producing same |
| CN111655890A (en) * | 2018-03-30 | 2020-09-11 | 日铁不锈钢株式会社 | Ferritic stainless steel sheet and method for producing same |
| JP2020164956A (en) * | 2019-03-29 | 2020-10-08 | 日鉄ステンレス株式会社 | Ferritic stainless steel sheet and manufacturing method therefor |
| WO2021065738A1 (en) * | 2019-10-02 | 2021-04-08 | 日鉄ステンレス株式会社 | Ferritic stainless steel sheet, method for producing same and ferritic stainless steel member |
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| CN101437974A (en) * | 2006-05-09 | 2009-05-20 | 新日铁住金不锈钢株式会社 | Stainless steel excellent in corrosion resistance, ferritic stainless steel excellent in resistance to crevice corrosion and formability, and ferritic stainless steel excellent inresistance to crevice |
| TW201435098A (en) * | 2013-02-04 | 2014-09-16 | Nippon Steel & Sumikin Sst | Ferritic stainless steel sheet with excellent workability and process for producing same |
| CN111655890A (en) * | 2018-03-30 | 2020-09-11 | 日铁不锈钢株式会社 | Ferritic stainless steel sheet and method for producing same |
| JP2020164956A (en) * | 2019-03-29 | 2020-10-08 | 日鉄ステンレス株式会社 | Ferritic stainless steel sheet and manufacturing method therefor |
| WO2021065738A1 (en) * | 2019-10-02 | 2021-04-08 | 日鉄ステンレス株式会社 | Ferritic stainless steel sheet, method for producing same and ferritic stainless steel member |
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