TW500811B - Austenitic stainless steel excellent in fine blankability - Google Patents
Austenitic stainless steel excellent in fine blankability Download PDFInfo
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- TW500811B TW500811B TW090111646A TW90111646A TW500811B TW 500811 B TW500811 B TW 500811B TW 090111646 A TW090111646 A TW 090111646A TW 90111646 A TW90111646 A TW 90111646A TW 500811 B TW500811 B TW 500811B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
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Abstract
Description
500811 五、發明説明（1 ) 發明背署 本發明關係一種原壞性（可衝切性）優異之沃斯田不銹鋼 ’尤其對於細緻之可衝切性。500811 V. Description of the invention (1) Invention invention The invention relates to a Vostian stainless steel which is excellent in originality (punctability), and is especially suitable for fine punchability.
剪切方法，特別是衝切，曾用壓機施行於各種金屬板料 ’其如普通鋼、不銹鋼和非鐵金屬，從而可依目的形狀有 效決定各種金屬板料之尺寸。然而，衝切所成平面有毛邊 而使尺寸精度久佳，金屬板料常在其較廣之表面發生減薄 現象’金屬板之厚度被減小於接近衝切面之部份。 對於需要高尺寸精度之產品，在製程中採用衝切時，衝 切面須以諸如滾磨加工之後處理予以硏磨。此項後處理基 本上是外加之程序而造成不良之生產力。爲此，曾經採用 一種細緻之衝切法以製造具有高尺寸精度之產品。在細緻 衝切法中，所訂餘隙値甚小以抑制破裂面之形成，金屬之 流入被限制以減少在衝切中發生薄邊化之現象。Shearing methods, especially punching, have been applied to various metal sheets using presses, such as ordinary steel, stainless steel, and non-ferrous metals, so that the size of various metal sheets can be effectively determined according to the desired shape. However, the plane formed by punching has burrs to make the dimensional accuracy better, and the metal sheet is often thinned on its wider surface. The thickness of the metal sheet is reduced to a portion close to the punched surface. For products requiring high dimensional accuracy, when punching is used in the manufacturing process, the punched surface must be honed by processing such as barrel grinding. This post-processing is basically an additional process that causes poor productivity. For this reason, a detailed die-cutting method has been used to manufacture products with high dimensional accuracy. In the detailed die-cutting method, the clearance is set to be very small to suppress the formation of the fracture surface, and the inflow of metal is restricted to reduce the phenomenon of thinning during punching.
另一方面，不銹鋼一直被用於在曝於腐蝕或高溼之環境 ，特別是SUS 304是適合此項用途而具有代表性。 SUS 304沃斯田不銹鋼是硬質材料，所以細緻之衝切模 頭尋命被縮短。SUS 304沃斯田不銃鋼之硬質也造成破裂 面比率之增加，有損衝切面之品質，而且加大薄邊化現象 。甚至如果以衝切形成高尺寸精度之剪切面，其作業成本 高於衝切普通鋼之成本。基於種種不利條件，SUS 3 04沃 斯田不銹鋼是用習知方法衝切而後硏磨，始能製成具有高 尺寸精度衝切面之產品。 潑明之槪述 500811 五、發明説明（2 ) 本發明目的在於提供一種沃斯田不銹鋼，其沃斯田相之 軟化與穩定性受到控制以使加大剪切面之比率，特別適合 用於細緻之衝切。 本發明提供一種新穎的沃斯田不銹鋼，所具組成含有最 高爲0.060質量％2(C + 1/2N)，最高爲1.0質量％之Si， 最高爲5質量％之Μη，最高爲0.060質量％之S，15〜20 質量％之Cr，5〜12質量％之Ni，最高5質量％之Cu，0 〜3.0質量％之Mo而餘量主要爲Fe。一種數値Md3G，代 表一種由應變引起的麻田散相之比率，由下式定義而在 -60至-10之範圍內調整。On the other hand, stainless steel has been used in environments exposed to corrosion or high humidity, and SUS 304 is particularly suitable for this purpose. SUS 304 stainless steel is a hard material, so the detailed die-cutting die life is shortened. The hardness of SUS 304 Worsfield stainless steel also causes an increase in the fracture surface ratio, which degrades the quality of the punched surface, and increases the phenomenon of thinning. Even if a cutting surface with high dimensional accuracy is formed by punching, the operation cost is higher than the cost of punching ordinary steel. Based on various unfavorable conditions, SUS 3 04 Vostian stainless steel is punched by conventional methods and then honed to produce products with high dimensional accuracy. Preface to the description 500811 V. Description of the invention (2) The purpose of the present invention is to provide a Vosstian stainless steel whose softening and stability are controlled so as to increase the ratio of the shearing surface, and is particularly suitable for detailed Of die cutting. The invention provides a novel Vostian stainless steel with a composition containing a maximum of 0.060% by mass 2 (C + 1 / 2N), a maximum of 1.0% by mass of Si, a maximum of 5% by mass, and a maximum of 0.060% by mass. S, 15 to 20% by mass of Cr, 5 to 12% by mass of Ni, up to 5% by mass of Cu, 0 to 3.0% by mass of Mo, and the balance is mainly Fe. A type of Md3G, which represents a ratio of scattered fields in Asada caused by strain, is defined by the following formula and adjusted within the range of -60 to -10.
Md30=5 5 1 -432(C+N)-9.2Si-29(Ni + Cu)-8.1Mn-13.7Cr-18.5Mo 沃斯田不銹鋼是以涉及熱乳、退火、酸洗、冷軋和最後 退火等習用製法所製成。在冷軋狀態中所增加之硬度比率 最好控制於20%或更高之維克氏硬度。在最後退火狀態之 不銹鋼較佳者處於晶粒數（Grain size number)(JIS G 055 1 所規定）爲8-11範圍內之結構。 圖式簡說 第1圖爲一示意圖，說明在衝切件中薄邊之產生和用於 檢測薄邊部份之位置。 第2圖爲一示意圖，說明在產品衝切面上剪切面之形成 和用於量測剪切面之位置。 第3圖爲座標圖，表示Md3〇値與剪切面比率之關係。 第4圖爲座標圖，表示（C+1/2N)與剪切面比率之關係。 第5圖爲座標圖，表示S含量與在餘隙率爲2%處剪切 -4- 500811 五、發明説明（3 ) 面比率之關係。 第6圖爲座標圖，表示S含量與餘隙率爲5%處剪切面 比率之關係。 第7圖爲座標圖，表示維克硬度與剪切面比率之關係。 第8圖爲座標圖，表示因回火輥軋而造成之硬度增大與 剪薄比之關係。 第9圖爲座標圖，表示晶粒數與剪切面比率之關係。 第1 〇圖爲座標圖，表示晶粒數與剪薄比之關係。 較佳具體例之詳細說明 發明人等在沃斯田不銹鋼之材料性質與由細緻衝切所形 成之衝切面狀況之關係上，從各種觀點加以硏究，發現回 應變引起之麻田散（α吋目）之比率在剪切面對衝切面之比例 有明顯之影響。 應變引起之麻田散（α (相）與沃斯田（r相）基質比較，爲 比較硬而延性低劣。過份產生應力引起之麻田散（α ·相）意 指延性劣化，在衝切面早發破裂，並減低剪切面之比率。 反之，如果應力引起之麻田散（6Τ相）之產生太少，沃斯田 不銹鋼在衝切時則如在r相中延性低劣，造成衝切面破裂 之早發，並減少剪切面之比例。 沃斯田不銹鋼之軟度是用在破裂面品質與應力所引起沃 麻田散（α '相）之效果予以適當之平衡，使得抑制薄邊化之 發生。所以，衝切面在尺寸精度上獲得改善，模頭壽命得 以延長。 所建議之沃斯田不銹鋼含有各種合金成份，其預定之比 500811 五、發明説明（4 ) 例如下： (C+1/2N)最高 0.060 質量 ％ C和N爲有效調製沃斯田相穩定性之成分，然而，過量 加入C和N將造成沃斯田相由於溶液硬化物而較硬，而且 亦使應力所引起之麻田散相比較硬。硬化促使衝切之負荷 加大而縮短模頭之壽命。因此（C+1/2N)之比率控制在0.060 質量％或較小。Md30 = 5 5 1 -432 (C + N) -9.2Si-29 (Ni + Cu) -8.1Mn-13.7Cr-18.5Mo Vostian stainless steel is involved in hot emulsion, annealing, pickling, cold rolling and finally Made by conventional manufacturing methods such as annealing. The increased hardness ratio in the cold-rolled state is preferably controlled to a Vickers hardness of 20% or more. The stainless steel in the final annealing state preferably has a structure in which the grain size number (specified by JIS G 055 1) is in the range of 8-11. Brief Description of the Drawings Figure 1 is a schematic diagram illustrating the generation of thin edges in a punched part and the position for detecting the thin edges. Figure 2 is a schematic diagram illustrating the formation of the shear surface on the die-cutting surface of the product and the position for measuring the shear surface. Figure 3 is a graph showing the relationship between Md303 and the ratio of the shear plane. Figure 4 is a graph showing the relationship between (C + 1 / 2N) and the ratio of the shear plane. Figure 5 is a graph showing the relationship between the S content and the shear at a clearance rate of 2%. Figure 6 is a graph showing the relationship between the S content and the shear plane ratio at a clearance rate of 5%. Fig. 7 is a graph showing the relationship between the Vickers hardness and the shear plane ratio. Figure 8 is a graph showing the relationship between the increase in hardness caused by temper rolling and the shear thinning ratio. Figure 9 is a graph showing the relationship between the number of grains and the ratio of the shear plane. Figure 10 is a graph showing the relationship between the number of grains and the shear thinning ratio. Detailed description of the preferred specific examples The inventors investigated from various viewpoints on the relationship between the material properties of Vostian stainless steel and the state of the punching surface formed by detailed punching, and found that Asa San (α inch The ratio of mesh) has a significant effect on the ratio of shear to punching. The strain-induced Asada San (α (phase)) is relatively hard and inferior to the Vostian (r-phase) matrix. The As Tian San (α · phase) caused by excessive stress means that the ductility is deteriorated, which is early on the punching surface. Breakage and reduce the ratio of the shear plane. Conversely, if the stress-induced production of Asada (6T phase) is too little, Vostian stainless steel is inferior in ductility in the r-phase during punching, causing the punched surface to rupture. Early onset and reducing the proportion of the shearing surface. The softness of Vostian stainless steel is used to properly balance the effect of the Wamatian San (α 'phase) caused by the quality of the fracture surface and the stress, so as to suppress the occurrence of thinning. . Therefore, the dimensional accuracy of the die-cutting surface is improved, and the die life is prolonged. The proposed Vostian stainless steel contains various alloy components with a predetermined ratio of 500811. 5. Description of the invention (4) For example: (C + 1 / 2N) Up to 0.060% by mass C and N are ingredients that effectively modulate the stability of the Voss field. However, excessive addition of C and N will cause the Voss field to be harder due to solution hardening, and it will also cause stress in the field. Scattered It is relatively hard. Hardening will increase the load of die cutting and shorten the life of the die. Therefore, the ratio of (C + 1 / 2N) is controlled to 0.060% by mass or less.
Si最局1.0質量％Si most round 1.0% by mass
Si是一種在煉鋼步驟中作爲去氧化劑而加之合金成分。 過量加入Si將造成沃斯田相因溶液硬化而比較硬，並使 不銹鋼之可衝切性劣化。爲此，Si含量之上限爲1.0質 量％)。 Μη最高5質量％ Μη爲用於穩定沃斯田相並改善不銹鋼可衝切性之有效 合金成分。增加Μη含量將使此等效果明顯。但是，過量 加入Μη而超過5質量％者，將造成非金屬夾雜物，對於 抗腐蝕性和可加工性相害。 S最高0.006質量％ S含量增加則剪切面對衝切面之比減小。S元素也對不 銹鋼最重要之性質抗腐飩性有有害之影響。因此，S含量 之上限訂爲0.006質量％。尤其，對於應具有高尺寸精度 衝切面之產品，S含量較好控制在0.003質量％或更小， 使剪切面之比率加大。Si is an alloying component added as a deoxidizing agent in the steel making step. Excessive addition of Si will cause the Vostian phase to be relatively hard due to solution hardening, and to deteriorate the punchability of stainless steel. For this reason, the upper limit of the Si content is 1.0% by mass). Mn up to 5% by mass Mn is an effective alloy composition for stabilizing the Voss phase and improving the punchability of stainless steel. Increasing the Mη content will make these effects obvious. However, if Mn is added in an excessive amount exceeding 5% by mass, non-metallic inclusions will be caused and the corrosion resistance and workability will be adversely affected. The highest S content is 0.006% by mass. The increase in the S content decreases the ratio of the shearing surface to the punching surface. The S element also has a deleterious effect on the corrosion resistance of stainless steel, the most important property. Therefore, the upper limit of the S content is set to 0.006% by mass. In particular, for products that should have high dimensional accuracy for the punched surface, the S content is preferably controlled to 0.003 mass% or less, so that the ratio of the sheared surface is increased.
Cr : 15-20 質量 ％ 500811 五、發明説明（5 ) 1 5質量％或更多之Cr含量爲確保不銹鋼抗腐蝕性所必 需。但是，過量加入多於20質量％之Cr將造成不銹鋼更 硬而對模頭壽命有不良影響。Cr: 15-20% by mass 500811 5. Description of the invention (5) 15% by mass or more of Cr is necessary to ensure the corrosion resistance of stainless steel. However, excessive addition of more than 20% by mass of Cr will make the stainless steel harder and adversely affect the life of the die.
Ni : 5-12 質量％ N i爲用於穩定沃斯田相之合金元素。此項效果顯現於 Ni之加入在5質量％或更多之比率。不銹鋼之可衝切性也 因Ni含量之增加而獲改善。然而，因Ni爲昂貴之元素而 增加鋼之成本，所以Ni含量之上限訂爲12質量％。Ni: 5-12% by mass Ni is an alloying element for stabilizing the Voss phase. This effect is exhibited when Ni is added at a ratio of 5 mass% or more. The punchability of stainless steel is also improved by increasing the Ni content. However, since Ni is an expensive element and the cost of steel is increased, the upper limit of the Ni content is set to 12% by mass.
Cu最局爲5質量％Cu is 5 mass%
Cu爲用於有效改善可衝切性並穩定沃斯田相之合金元 素。然而，過量加入Cu而多於5質量％，將對熱加工性 有不良之影響。Cu is an alloy element for effectively improving punchability and stabilizing the Voss phase. However, if Cu is added in an excessive amount of more than 5% by mass, the hot workability will be adversely affected.
Mo : 0-3.0 質量 ％Mo: 0-3.0% by mass
Mo爲用於有效改善抗腐蝕性之任意加入之合金元素。 但是多於3.0質量％而過量加入Mo，將使不銹鋼太硬，造 成細緻可衝切性之劣化。Mo is an optional added alloy element for effectively improving corrosion resistance. However, if Mo is added in excess of 3.0% by mass, the stainless steel will be too hard, and the fine die-cutability will be deteriorated.
Md3G値（代表應變所引起之麻田散之比率）：-60至-10 應變所引起之麻田散U ’相）對於剪切面與衝切面比率之 影響，是發明人經各項實驗所發現的結果。應變所引起之 麻田散（α ’相）之比率可以經沃斯田不銹鋼之成分和含量計 算。如果所設計之沃斯田不銹鋼組成具有控制在-60至-10 範圍內之Md3()値，則剪切面之比率較高而如以下各實施 例所說明，且衝切面以高的尺寸精度而形成。 沃斯田不銹鋼硬度增大的比率： 維克硬度爲20%或更高 冷軋沃斯田不銹鋼板與轉變較少之退火鋼板比較’由方令 500811 五、發明説明（6 ) 在冷軋中導入多種轉變而較硬。若因冷軋所造成之硬化程 度被調整至20%或更高之維克氏硬度，流向衝切低部之金 屬受到抑制，導致薄邊化減少。 在本說書中硬度增大之比率定義如下式：[冷乳鋼板 之維克硬度]-(退火鋼板之維克硬度）]/(退火鋼板之維克硬 度）x 100(%)。20%或更高之硬度增大比率是抑制因衝切所 造成而發生薄邊化所必需，使達於衝切已退火鋼板時所生 之薄邊化之一半或更少。然而，在衝切當中極度硬化之鋼 板造成抗剪力之增加而提高模頭之磨耗。因此，硬度增高 之比率上限較佳訂爲1 50%，說明薄邊化之減少而與模頭 壽命平衡之效果。 晶粒數：#8至#11 當晶粒被粗化，不銹鋼變軟而剪切面對衝切面之比率較 高，但是被衝切之鋼板有嚴重的薄邊化。因此，對於製造 在衝切面以及平滑度等應具尺寸精度之產品，粗大晶粒並 不理想。另一方面，所建議之沃斯田不銹鋼被調整至金相 結構中含有被最小化之晶粒，在最後退火狀態中晶粒數在 #8至#11之範圍內。該晶粒數與一般#6至#8之晶粒數比 較爲較大。最小化之晶粒被認爲是因輸入能量減少，例如 不銹鋼退火於比較低之溫度或於比較短之時間。由於晶粒 大小之如此調整，薄邊化之發生到抑制而剪切面之比率保 持於相同之水準。 實施例1 具有表1所示組成之各種不銹鋼被熔融，鑄造，均熱於 500811 五、發明説明（7 ) 123CTC，並熱軋至10毫米厚度。其後，熱軋鋼板退火於 11 50t 1分鐘，用酸浸洗，冷軋至5毫米厚度，退火於 1 050°C 1分鐘並再用酸浸洗。 500811 五、發明説明（） 註記 發明之 實施例 比較例 發明之 實施例 比較例 發明 實施例 比較例 T3 -37.1 -43.8 -35.6 〇6 rn -40.3 -14.3 —57.5 -62.5 -75.3 -8.0 15.0 -22.9 -47.2 -33.8 1 -33.9 -15.2 Μ _( Φ 4π 0.01 0.03 0.03 0.05 0.01 0.01 0.02 0.01 0.02 0.01 0.04 1 0.02 1 0.02 0.02 0.02 0.02 〇 0.08 0.07 0.07 0.06 0.07 0.08 0.05 0.08 0.08 0.08 0.08 0.08 i 0.09 0.07 0.09 0.09 5 0.10 2.10 1.92 0.10 3.21 0.08 0.08 0.10 0.10 0.10 0.10 0.81 0.10 0.10 0.08 0.08 C/D 0.001 0.003 0.002 0.001 0.001 0.002 0.002 0.001 0.001 0.001 0.001 0.001 0.004 0.006 I ! 0.007 1 1 0.009 18.25 18.70 18.10 17.16 17.10 18.26 18.42 19.10 18.33 18.25 18.25 18.25 18.91 19.10 18.91 1 19.10 10.75 8.21 8.32 10.23 8.01 10.01 11.15 11.20 11.82 9.83 8.21 8.81 10.27 9.89 10.27 9.21 G S Ο (Ν Ο ο r- 〇 〇〇 t—< in 〇 Ο O 00 o o OO Ό o 〇 ιη ο ο ο 寸 ο rn ^ o o o 〇 o o o ^ SO o o o 寸· 々 o o u 0.01 0.02 0.03 寸· ο 0.02 0.01 0.02 0.01 0.02 0.01 0.03 0.05 0.03 0.02 0.01 0.03 試樣 編號 ^ (Ν m 寸 VD 卜 ^ 2 ^ (N m 寸 τ—i r—( t—^ ............. 500811 五'發明説明（9 ) 各種已退火之鋼板用下列衝切試驗檢驗以硏究抗剪切性 ，剪切面對衝切面比率，和薄邊對厚度比率，以及依Jis Z 2240所規定之洛氏B硬度量測其維克氏硬度。 從各已退火鋼板切取試片，用外徑50毫米之衝頭和內 徑爲50.2毫米或50.5毫米之模頭，以600毫米/分之衝切 速率衝切一餘隙爲0.1毫米或0.25毫米之碟形（餘隙比率 以試片之餘隙/厚度計算，分別爲2%或5%)。 各碟（衝切件）用雷射型非接觸性位置感應器量測8點， 亦即在沿輥軋方向、和分別與輥軋方向正交之方向及成45 度傾斜之方向各2點，如第1圖所示，測出各點薄邊Z之 程度。平均各量測値，計算薄邊對厚度之比率，如平均値 對試件厚度之比率。 各碟（衝切件）之剪切面S之厚度亦量測8點，亦即在沿 輥軋方向、和分別與輥軋方向正交之方向及成45度傾斜 之方向各2點，如第2圖所示。平均量測之値，計算剪切 面比率，如平均値對試件厚度之比率。 具有2%餘隙比各試件以衝切所形成剪切面之比率，其 與各試件之Md3〇値之關係，經過硏究，結果如第3圖所 示。其所表示，具有100%剪切面比率之衝切面獲得在-60 至-10範圍內之Md3。値。雖然試樣第4、15和16號具有 在-60至-10範圍內之Md3〇値，其衝切面極度不良而剪切 面比率分別爲85%，95%和71%。 (C+1/2N)與剪切面比率之關係經過硏究，如試樣1 -4 和12各具有在-60至-10範圍內之Md3〇値。結果如弟4圖 -11- 500811 五、發明説明（1Q ) 所示。其所表示者爲第1-3及12各試樣含有少於〇·06質 量％之（〇+1/2”，經衝切而有100%之剪切面比率。另一方 面，試樣4含多於〇.〇6質量％2(C+1/2N)，經衝切而有 85%之剪切面比率。 試樣第1-3號和13-16號具有在-60至-10範圍內之 Md3G値，並含有少於〇.〇6質量％2(C + 1/2N)，經過以2% 之餘隙比衝切。由衝切所形成之剪切面比率經過硏究，其 與試樣之S含量之關係，結果見於第5圖，爲表示試樣第 1-3，13和14號含S少於0.006質量％，經以100%之剪切 面比率衝切，而試樣第15和16號含S多於0.006質量％ 者，以分別爲95%和71%之剪切面比率衝切。 S含量與剪切面比率之關係亦隨餘隙比率而改變，甚至 在衝切同一鋼板。此即，當試樣第13和14號用2%餘隙 比衝切，衝切面於剪切面比率爲100%時形成。當試樣第 1 3和1 4號用5%餘隙比衝切，則剪切面比率分別減至92% 和88%，如第6圖所示。各項結果證明控制S含量少於 0.003質量％，可以用以促使減少剪切面比率之大餘隙比 ，有效衝切鋼板。 實施例2 具有如表2所示組成之不銹鋼，經過熔融，鑄造，熱軋 於123 t之初始溫度至10毫米厚度。然後，各已熱乳之鋼 板被退火於1150°C 1分鐘，酸洗，冷軋至中等厚度5-8毫 米，於1 05 0°C退火1分鐘，再酸洗。若干厚度5毫米之鋼 板被供作已退火鋼板（A1，B1)。其他中等厚度已退火鋼板 -12- 500811 五、發明説明（n ) ^ 再被冷軋至5毫米厚度，並供作回火輥軋之鋼板（A2-A6, B2，B3)。 表2 :用於實施例2之沃斯田不銹鋼 鋼板 種類 合金, 成分（質量％) Md3〇 註記 C Si Μη Ni Cr S Cu Mo N A 0.01 0.5 0.8 10.43 18.40 0.001 0.09 0.07 0.01 -27.8 發明之 實施例 B 0.06 0.6 0.6 8.02 18.21 0.003 0.08 0.08 0.04 8.6 比較例 從各已退火並回火輥軋之鋼板切取一試片，並用2%餘 隙比於與實施例1相同條件下衝切。第7圖表示各試片之 維克硬度與剪切面比率之關係。其所表示爲任何已退火或 回火輥軋之試樣第A1至A6號用100%之剪切面比率衝切 。另一方面，試樣B1至B3對應於SUS 304者用近於 45%之低剪切面比率衝切。 剪切薄邊比率是以（在回火輥軋之鋼板中薄邊對厚度比 率）/(在退火鋼板中薄邊對厚度比率）予以計算，硏究回火 輥軋增加之硬度對產生薄邊化之影響。結果如第8圖所示 。其所表示爲任何回火輥軋鋼板A3至A6以20%或更高 之維克氏硬度硬化者，其剪切薄邊比小於50%，亦即，小 於在退火鋼板A1中所產生薄邊之一半。另一方面，回火 輥軋鋼板A2以小於20%之硬度增加比較化者，其剪切薄 邊比與退火鋼板A1比較，約爲70%。此等結果證明硬度 增加20%或更高，對於充份減少薄邊化爲有效。 各試片繼續被衝切直至更換模頭，硏究鋼板材料性質與 模頭壽命之影響。模頭壽命是以各次衝切循環直至更換模 -13- 500811 五、發明説明（12 ) 頭而評定。結果見於表3 其所表示爲任何A型鋼板與B 型鋼板比較，可以以較大循環次數衝切直至更換模頭。此 即，A型鋼板可有效延長模頭壽命。其亦表示各A型鋼板 之比較，其硬度增加不宜過份致使衝切循環減少。例如， 對於硬化高於150%之A6鋼板，其至更換模頭之衝切循環 數有所減少。 表3 :鋼板之材料性質對模頭壽命之影響Md3G 値 (represents the ratio of Asada San caused by strain): -60 to -10 The effect of Asa San U 'phase caused by strain) on the ratio of the shear plane to the punched plane was discovered by the inventor through various experiments result. The strain-induced ratio of Asada powder (α 'phase) can be calculated from the composition and content of Vostian stainless steel. If the designed Wastfield stainless steel composition has Md3 () 値 controlled in the range of -60 to -10, the ratio of the shearing surface is high as explained in the following examples, and the punching surface has high dimensional accuracy And formed. The rate of increase in hardness of Vostian stainless steel: Vickers hardness of 20% or higher Cold-rolled Vostian stainless steel plate compared with annealed steel plate with less transformation 'by Order 500811 V. Description of invention (6) In cold rolling Harder to introduce multiple transitions. If the degree of hardening caused by cold rolling is adjusted to Vickers hardness of 20% or higher, the flow of metal to the lower part of the blanking is suppressed, resulting in a reduction in thinning. The ratio of hardness increase in this storybook is defined as follows: [Vicker hardness of cold-rolled steel sheet]-(Vicker hardness of annealed steel sheet)] / (Vicker hardness of annealed steel sheet) x 100 (%). A hardness increase ratio of 20% or more is necessary to suppress the thinning caused by punching, so that the thinning caused by punching of the annealed steel sheet is one-half or less. However, the extremely hardened steel sheet during die cutting increases the shear resistance and increases the wear of the die. Therefore, the upper limit of the ratio of hardness increase is preferably set to 150%, which indicates the effect of reducing the thinning and balancing the life of the die. Number of grains: # 8 to # 11 When the grains are roughened, the stainless steel becomes soft and the ratio of the sheared surface to the punched surface is high, but the steel sheet being punched has severe thinning. Therefore, coarse-grained grains are not ideal for products that should have dimensional accuracy in terms of punching surface and smoothness. On the other hand, the proposed Wastfield stainless steel is adjusted so that the metallographic structure contains minimized grains, and the number of grains in the final annealing state is in the range of # 8 to # 11. This number of grains is larger than the number of grains of # 6 to # 8 in general. Minimized grains are considered to be due to reduced input energy, for example, stainless steel is annealed at a lower temperature or a shorter time. Because of the adjustment of the grain size, the occurrence of thinning is suppressed and the ratio of the shear plane is maintained at the same level. Example 1 Various stainless steels having the composition shown in Table 1 were melted, cast, and all heated to 500811. V. Description of the Invention (7) 123CTC, and hot rolled to a thickness of 10 mm. Thereafter, the hot-rolled steel sheet was annealed at 11 50 t for 1 minute, leached with acid, cold-rolled to a thickness of 5 mm, annealed at 1 050 ° C for 1 minute, and then leached with acid. 500811 V. Description of the invention () Note the example of the invention, the comparative example of the invention, the comparative example of the invention, the comparative example of the invention, T3 -37.1 -43.8 -35.6 〇6 rn -40.3 -14.3 -57.5 -62.5 -75.3 -8.0 15.0 -22.9 -47.2 -33.8 1 -33.9 -15.2 M _ (Φ 4π 0.01 0.03 0.03 0.05 0.01 0.01 0.02 0.01 0.02 0.01 0.04 1 0.02 1 0.02 0.02 0.02 0.02 〇0.08 0.07 0.07 0.06 0.07 0.08 0.0 0.05 0.08 0.08 0.08 0.08 0.08 0.08 0.08 0.09 0.09 0.09 5 0.10 2.10 1.92 0.10 3.21 0.08 0.08 0.10 0.10 0.10 0.10 0.81 0.10 0.10 0.08 0.08 C / D 0.001 0.003 0.002 0.001 0.001 0.002 0.002 0.001 0.001 0.001 0.001 0.001 0.004 0.006 I! 0.007 1 1 0.009 18.25 18.70 18.10 17.16 17.10 18.26 18.42 19.10 18.33 18.25 18.25 18.25 18.91 19.10 18.91 1 19.10 10.75 8.21 8.32 10.23 8.01 10.01 11.15 11.20 11.82 9.83 8.21 8.81 10.27 9.89 10.27 9.21 GS Ο (Ν Ο ο r- 〇〇〇t— < in 〇O O 00 oo OO Ό o 〇ιη ο ο ο inch ο rn ^ ooo 〇ooo ^ SO ooo inch · 々oou 0.01 0.02 0.03 inch · ο 0.02 0.01 0.02 0.01 0.02 0.01 0.03 0.05 0.03 0.02 0.01 0.03 Sample number ^ (N m inch VD ^ 2 ^ (N m inch τ—ir— (t— ^ ............. 500811 Five 'invention description (9 ) Various annealed steel plates are tested by the following punching tests to investigate the shear resistance, the ratio of the shearing surface to the punching surface, and the ratio of thin edge to thickness, and the dimensions are measured according to Rockwell B hardness specified by Jis Z 2240. Kickers hardness. Cut test pieces from each annealed steel sheet, and use a punch with an outer diameter of 50 mm and a die with an inner diameter of 50.2 mm or 50.5 mm to punch a clearance of 0.1 mm or 0.25 mm at a punching rate of 600 mm / min. Dish shape (clearance ratio is calculated by the clearance / thickness of the test piece, respectively 2% or 5%). Each dish (blanket) is measured with laser-type non-contact position sensor at 8 points, that is, 2 points each in the rolling direction, the direction orthogonal to the rolling direction, and the direction inclined at 45 degrees. As shown in Figure 1, the extent of the thin edge Z at each point is measured. Measure the average 値, calculate the ratio of thin edge to thickness, such as the ratio of average 値 to thickness of the test piece. The thickness of the cutting surface S of each dish (blanking part) is also measured at 8 points, that is, 2 points each in the rolling direction, the direction orthogonal to the rolling direction, and the direction inclined at 45 degrees, such as Figure 2 shows. Calculate the ratio of the shear plane, such as the ratio of the average ratio to the thickness of the test piece. The ratio of 2% clearance to the shear surface formed by punching of each test piece, and the relationship with the Md30 値 of each test piece, after investigation, the results are shown in Figure 3. It states that a die-cut surface with a 100% shear surface ratio obtains Md3 in the range of -60 to -10. value. Although Sample Nos. 4, 15, and 16 had Md3O 値 in the range of -60 to -10, the punching planes were extremely poor and the shear plane ratios were 85%, 95%, and 71%, respectively. The relationship between (C + 1 / 2N) and the shear plane ratio has been studied, for example, samples 1-4 and 12 each have an Md3O 値 in the range of -60 to -10. The results are shown in Figure 4-11-11 500811 5. Invention Description (1Q). What it means is that each of the samples 1-3 and 12 contains less than 0.06 mass% (0 + 1/2 ", and has a shear surface ratio of 100% after punching. On the other hand, the sample 4 contains more than 0.05% by mass 2 (C + 1 / 2N), and has a shear surface ratio of 85% after punching. Sample Nos. 1-3 and 13-16 have between -60 and- Md3G 値 in the range of 10, and contains less than 0.06% by mass 2 (C + 1 / 2N), after punching with a clearance ratio of 2%. The ratio of the shear surface formed by punching is researched The relationship between the S content of the sample and the result is shown in Figure 5. In order to show that the samples No. 1-3, 13 and 14 contain S less than 0.006% by mass, they are punched at a shear surface ratio of 100%. The samples No. 15 and No. 16 containing S more than 0.006% by mass are die-cut with a shear surface ratio of 95% and 71%, respectively. The relationship between the S content and the shear surface ratio also changes with the clearance ratio. Even when punching the same steel sheet. That is, when samples No. 13 and No. 14 are die-cut with a clearance ratio of 2%, the ratio of the punched surface to the shear plane is 100%. When samples No. 13 and No. 14 When punching with a 5% clearance ratio, the shear plane ratios are reduced to 92% and 88%, as shown in Figure 6. It is proved that controlling the S content to less than 0.003 mass% can be used to promote the reduction of the large clearance ratio of the shear surface ratio and effectively punch the steel sheet. Example 2 A stainless steel having the composition shown in Table 2 is melted, cast, and hot rolled. At an initial temperature of 123 t to a thickness of 10 mm. Then, each hot-milk steel sheet is annealed at 1150 ° C for 1 minute, pickled, cold rolled to a medium thickness of 5-8 mm, and annealed at 1 05 0 ° C for 1 minute. , And then pickling. Several 5 mm thick steel plates are provided as annealed steel plates (A1, B1). Other medium thickness annealed steel plates-12- 500811 5. Description of the invention (n) ^ is cold rolled to 5 mm thickness, It is also used as a tempered rolled steel sheet (A2-A6, B2, B3). Table 2: The type of alloy used in Example 2 of the Wastfield stainless steel sheet, composition (mass%) Md3. Note C Si Mn Ni Cr S Cu Mo NA 0.01 0.5 0.8 10.43 18.40 0.001 0.09 0.07 0.01 -27.8 Example B of the invention 0.06 0.6 0.6 8.02 18.21 0.003 0.08 0.08 0.04 8.6 Comparative Example A test piece was cut from each annealed and tempered steel sheet, and 2% was used. The clearance ratio is blanked under the same conditions as in Example 1. No. 7 The figure shows the relationship between the Vickers hardness and the shear surface ratio of each test piece. It shows that any of the annealed or tempered samples No. A1 to A6 are punched with a 100% shear surface ratio. Another In terms of specimens B1 to B3, corresponding to SUS 304, were die cut with a low shear surface ratio of approximately 45%. Shear thin edge ratio is calculated as (thin edge to thickness ratio in tempered rolled steel plate) / (thin edge to thickness ratio in annealed steel plate). The increase in hardness of tempered rolled steel produces thin edges. Of the impact. The results are shown in Figure 8. It means that any tempered rolled steel plates A3 to A6 are hardened with a Vickers hardness of 20% or higher, and the shear thin edge ratio is less than 50%, that is, less than the thin edge produced in the annealed steel plate A1. One and a half. On the other hand, in the case where the tempered rolled steel sheet A2 has a hardness increase of less than 20%, the shear thin edge ratio is about 70% compared with the annealed steel sheet A1. These results prove that an increase in hardness of 20% or more is effective for sufficiently reducing thinning. Each test piece is continuously punched until the die is replaced, and the influence of the properties of the steel plate material and the life of the die is investigated. Die life is evaluated by each die cutting cycle until the die is replaced. V. Invention Description (12) The head is evaluated. The results are shown in Table 3. It is shown that any type A steel plate is compared with the type B steel plate and can be punched with a large number of cycles until the die is replaced. That is, the A-type steel plate can effectively extend the life of the die. It also indicates that the comparison of various A-type steel plates should not increase the hardness excessively, resulting in a reduction in the punching cycle. For example, for A6 steel plates that are hardened above 150%, the number of die-cutting cycles to die replacement is reduced. Table 3: Influence of material properties of steel plate on die life
編號 直至更換模頭之衝切循環數 評估 註記 A1 302969 ◎ 發明之 實施例 A2 323341 ◎ A3 309629 ◎ A4 314211 ◎ A5 354824 ◎ A6 248142 〇 B1 103288 X 比較例 B2 52783 X B3 9879 X ◎:與A1鋼板比較，模頭壽命相同或較長 〇··模頭壽命不如A1鋼板，但優於B1鋼板 X :模頭明顯磨損 實施例3 具有表4所示組成之鋼板c，D被焙融，鑄造，並在初 始溫度熱軋至10毫米之厚度。然後，各已熱軋之鋼板在 Π 5 0°C退火1分鐘，酸洗，冷軋至5毫米厚度，在800-11 00°C退火1分鐘，然後再酸洗。 -14- 五、發明説明（13) 表‘ 4 :用於實施例3之沃斯田不銹鋼 試樣 編號 ———— — 合金 成分（質量％) Md3〇 註記 C Si Μη Ni Cr S Cu Mo N C 0.02 0.6 0.7 10.21 18.71 0.002 0.08 0.05 0.02 -34.3 發明之 實施例 〜D 0.06 0.6 0.6 8.02 18.21 0.003 0.08 0.08 0.04 8.6 比較例 從已退火後經酸洗之各鋼板切取試片，以2%之餘隙比 於與實施例1相同條件下衝切。在衝切之試片中衝切面之 比率經過計算以硏究其與鋼片晶粒數之關係，結果列於第 9圖。其所表示爲根據本發明之任何C型鋼板，用1 〇〇% 之剪切面比率衝切而無關於晶粒數。另一方面，任何相當 於SUS 3 04之D型鋼板用低於近45%衝切面比率衝切。 剪切薄邊比率與晶粒數之關係列於第1 0圖。此關係證 明剪切薄邊比之改良隨晶粒數（亦即最小化之全相結構而 增大，與鋼板之種類無關。對於根據本發明之C型鋼板， 具有大於#8之晶粒數之任何C3至C6鋼板，與晶粒數小 於#8之C 1，C2鋼板比較，前者之剪切薄邊比減少一半或 更小。 各試片繼續衝切以至更換模頭，用以從衝切循環數評估 模頭壽命，結果見於表5。其所表示爲任何C型鋼板可衝 切較多次之循環以至更換模頭，亦即比D型鋼板更適合用 於模頭壽命之延長。但是，衝切循環數在晶粒數增至大於 # 1 1時有所減少，如C6鋼板所示。此項結果證明金相結 構過份最小化不利於模頭壽命。 -15- 500811 五、發明説明（14) 表5 :模頭壽命與鋼板之材料性質之關係Number Note for the evaluation of the number of die-cutting cycles until the die is replaced A1 302969 ◎ Invention Example A2 323341 ◎ A3 309629 ◎ A4 314211 ◎ A5 354824 ◎ A6 248142 〇B1 103288 X Comparative Example B2 52783 X B3 9879 X ◎: Same as A1 steel plate By comparison, the die life is the same or longer. The die life is not as good as A1 steel plate, but better than B1 steel plate X: The die is significantly worn. Example 3 Steel plates c and D having the composition shown in Table 4 are melted and cast. It is hot rolled to a thickness of 10 mm at the initial temperature. Then, each hot-rolled steel sheet was annealed at Π 50 ° C for 1 minute, pickled, cold-rolled to a thickness of 5 mm, annealed at 800-11 00 ° C for 1 minute, and then pickled. -14- V. Description of the invention (13) Table '4: No. of Wastfield stainless steel sample used in Example 3 — — — Alloy composition (mass%) Md3〇 Note C Si Mn Ni Cu S Cu Mo NC 0.02 0.6 0.7 10.21 18.71 0.002 0.08 0.05 0.02 -34.3 Example of the invention ~ D 0.06 0.6 0.6 8.02 18.21 0.003 0.08 0.08 0.04 8.6 Comparative Example Cut a test piece from each steel sheet that has been annealed and pickled, with a clearance ratio of 2% Die cutting was performed under the same conditions as in Example 1. The ratio of the die-cut surface in the die-cut test piece was calculated to investigate its relationship with the number of grains in the steel sheet. The results are shown in Figure 9. It is shown that any C-shaped steel sheet according to the present invention is punched with a shear surface ratio of 1000% regardless of the number of crystal grains. On the other hand, any D-shaped steel sheet equivalent to SUS 3 04 is blanked with a blanking ratio of less than 45%. The relationship between the shear thin edge ratio and the number of grains is shown in Fig. 10. This relationship proves that the improvement of the shear thin edge ratio increases with the number of grains (that is, the minimized all-phase structure, regardless of the type of steel sheet. For the C-type steel sheet according to the present invention, it has a number of grains greater than # 8 For any C3 to C6 steel plate, compared with C1, C2 steel plate with less than # 8 grains, the shear thin edge ratio of the former is reduced by half or less. Each test piece continues to die cut or even replace the die head to change the die The number of cutting cycles is used to evaluate the life of the die. The results are shown in Table 5. It indicates that any C-shaped steel plate can be punched multiple times to replace the die. However, the number of die-cutting cycles decreases when the number of grains increases to # 1 1 as shown in the C6 steel plate. This result proves that excessive minimization of the metallurgical structure is not conducive to the life of the die. -15- 500811 V. Description of the invention (14) Table 5: Relation between die life and material properties of steel plate
編號 直至更換模頭之衝切循環數 評估 註記 C1 321962 ◎ 發明之 實施例 C2 339672 ◎ C3 321111 ◎ C4 342632 ◎ C5 315522 ◎ C6 236981 〇 D1 112011 X 比較例 D2 49876 X D3 562 1 X ◎:與A1鋼板比較，模頭壽命相同或更長 〇：模頭壽命不如A1鋼板，但優於B1鋼板 X :模頭明顯磨損 本發明所提出之一種沃斯田不銹鋼，由於優異之可衝切 性，尤其細緻之可衝切性，可以被衝切成爲有高尺寸精度 之產品。甚至在用小的餘隙比衝切鋼板時，可以保持高度 的剪切面對衝切面之比率而在實質上不發生薄邊化。不銹 鋼板與習用沃斯田不銹鋼板如SUS 304者比較，也有利於 模頭壽命之延長。因此，具有高尺寸精度之衝切產品可以 獲自所提議之沃斯田不銹鋼板而不增加製造成本。 -16-Note for evaluating the number of die-cutting cycles until the die is replaced C1 321962 ◎ Invention Example C2 339672 ◎ C3 321111 ◎ C4 342632 ◎ C5 315522 ◎ C6 236981 〇D1 112011 X Comparative Example D2 49876 X D3 562 1 X ◎: Same as A1 Compared with steel plates, the die life is the same or longer. 0: Die life is not as good as A1 steel plate, but better than B1 steel plate. X: The die head is obviously worn. A kind of Vostian stainless steel proposed by the present invention is particularly excellent in punchability. Fine punchability can be punched into products with high dimensional accuracy. Even when the steel sheet is blanked with a small clearance ratio, a high ratio of the sheared face to the blanked face can be maintained without thinning substantially. Compared with conventional stainless steel plates such as SUS 304, stainless steel plates are also beneficial to the extension of die life. Therefore, die-cutting products with high dimensional accuracy can be obtained from the proposed Vostian stainless steel plate without increasing manufacturing costs. -16-
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000142644A JP3691341B2 (en) | 2000-05-16 | 2000-05-16 | Austenitic stainless steel sheet with excellent precision punchability |
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| TW500811B true TW500811B (en) | 2002-09-01 |
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| US (1) | US20020015655A1 (en) |
| EP (1) | EP1156125B1 (en) |
| JP (1) | JP3691341B2 (en) |
| KR (1) | KR100421511B1 (en) |
| CN (1) | CN1145713C (en) |
| DE (1) | DE60122618T2 (en) |
| ES (1) | ES2270918T3 (en) |
| MY (1) | MY146900A (en) |
| SG (1) | SG108254A1 (en) |
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| JP2001131707A (en) * | 1999-10-29 | 2001-05-15 | Dainippon Printing Co Ltd | Shadow mask for color cathode-ray tube |
| AU2001276679A1 (en) * | 2000-08-01 | 2002-02-13 | Nisshin Steel Co. Ltd. | Stainless steel fuel tank for automobile |
| JP3696552B2 (en) * | 2001-04-12 | 2005-09-21 | 日新製鋼株式会社 | Soft stainless steel plate with excellent workability and cold forgeability |
| US20040265238A1 (en) * | 2003-06-27 | 2004-12-30 | Imtiaz Chaudry | Inhalable formulations for treating pulmonary hypertension and methods of using same |
| FR2864108B1 (en) * | 2003-12-22 | 2006-01-27 | Ugine Et Alz France | STAINLESS STEEL SHEET HAVING HIGH RESISTANCE AND LENGTH ELONGATION, AND METHOD OF MANUFACTURE |
| WO2006016010A1 (en) * | 2004-07-08 | 2006-02-16 | Ugine & Alz France | Austenitic stainless steel composition and use thereof for the production of structural parts for land transport means and containers |
| KR20070110081A (en) * | 2005-03-09 | 2007-11-15 | 머크 앤드 캄파니 인코포레이티드 | Quinazolinone t-type calcium channel antagonists |
| US20100066779A1 (en) | 2006-11-28 | 2010-03-18 | Hanan Gothait | Method and system for nozzle compensation in non-contact material deposition |
| AU2008275674A1 (en) * | 2007-07-10 | 2009-01-15 | Merck & Co., Inc. | Quinazolinone T-type calcium channel antagonists |
| JP5014915B2 (en) * | 2007-08-09 | 2012-08-29 | 日新製鋼株式会社 | Ni-saving austenitic stainless steel |
| EP2072631A1 (en) * | 2007-12-20 | 2009-06-24 | Ugine & Alz France | Austenitic stainless steel sheet and method for obtaining this sheet |
| CN101994068B (en) * | 2009-08-25 | 2012-12-26 | 宝山钢铁股份有限公司 | Austenitic stainless steel plate |
| JP5528459B2 (en) * | 2009-09-02 | 2014-06-25 | 新日鐵住金ステンレス株式会社 | Ni-saving stainless steel with excellent corrosion resistance |
| CN101791648A (en) * | 2010-04-10 | 2010-08-04 | 中精集团有限公司 | Process for stamping stainless steel thick plate |
| KR20120132691A (en) * | 2010-04-29 | 2012-12-07 | 오또꿈뿌 오와이제이 | Method for manufacturing and utilizing ferritic-austenitic stainless steel with high formability |
| KR101659186B1 (en) * | 2014-12-26 | 2016-09-23 | 주식회사 포스코 | Austenitic stainless steels with increased flexibility |
| KR101923922B1 (en) | 2016-12-23 | 2018-11-30 | 주식회사 포스코 | Austenitic stainless steel product having excellent surface properties and manufacturing method of the same |
| KR101964314B1 (en) * | 2017-08-21 | 2019-08-07 | 주식회사포스코 | Austenitic stainless steel with excellent workability and resistant of season cracking, and drawing product using the same |
| CN113265585B (en) * | 2021-05-14 | 2023-02-24 | 山西太钢不锈钢股份有限公司 | Stainless steel for automobile safety airbag and production method and application thereof |
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| JPS5856746B2 (en) * | 1980-04-15 | 1983-12-16 | 日本ステンレス株式会社 | Austenitic stainless steel with good press formability and corrosion resistance |
| JPH0768584B2 (en) * | 1986-06-09 | 1995-07-26 | 日新製鋼株式会社 | Manufacturing method of stainless steel for springs having excellent spring characteristics |
| JP3217088B2 (en) * | 1991-07-26 | 2001-10-09 | 三桜工業株式会社 | Stainless steel multiple winding pipe |
| EP0594866B1 (en) * | 1992-04-16 | 1998-08-05 | Nippon Steel Corporation | Austenitic stainless steel sheet with excellent surface quality and production thereof |
| KR950009223B1 (en) * | 1993-08-25 | 1995-08-18 | 포항종합제철주식회사 | Austenite stainless steel |
| JPH07180000A (en) * | 1993-12-22 | 1995-07-18 | Nkk Corp | Austenitic stainless steel sheet for floppy disk shutter and its production |
| JPH07216512A (en) * | 1994-01-31 | 1995-08-15 | Sumitomo Metal Ind Ltd | Austenitic stainless steel excellent in stress corrosion cracking resistance and deep drawability |
| JP3464297B2 (en) * | 1994-08-31 | 2003-11-05 | 日新製鋼株式会社 | Austenitic stainless steel sheet for high-speed warm drawing and its warm drawing method |
| JP3206631B2 (en) * | 1994-10-12 | 2001-09-10 | 日鉱金属株式会社 | Austenitic stainless steel with excellent roll transferability |
| JP3839108B2 (en) * | 1996-10-14 | 2006-11-01 | 日新製鋼株式会社 | Austenitic stainless steel with excellent workability after punching |
| JP3307841B2 (en) * | 1996-10-23 | 2002-07-24 | 山陽特殊製鋼株式会社 | Semi-austenite precipitation hardened stainless steel with excellent hydrochloric acid resistance and cold workability |
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- 2001-05-07 EP EP01110998A patent/EP1156125B1/en not_active Expired - Lifetime
- 2001-05-07 DE DE60122618T patent/DE60122618T2/en not_active Expired - Fee Related
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| MY146900A (en) | 2012-10-15 |
| KR100421511B1 (en) | 2004-03-09 |
| SG108254A1 (en) | 2005-01-28 |
| DE60122618D1 (en) | 2006-10-12 |
| CN1145713C (en) | 2004-04-14 |
| JP2001323342A (en) | 2001-11-22 |
| CN1327078A (en) | 2001-12-19 |
| EP1156125A2 (en) | 2001-11-21 |
| EP1156125B1 (en) | 2006-08-30 |
| EP1156125A3 (en) | 2002-01-30 |
| JP3691341B2 (en) | 2005-09-07 |
| DE60122618T2 (en) | 2007-09-27 |
| US20020015655A1 (en) | 2002-02-07 |
| KR20010105193A (en) | 2001-11-28 |
| ES2270918T3 (en) | 2007-04-16 |
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