TW522060B - Method for manufacturing a steel strip or sheet consisting mainly of Mn-austenite - Google Patents

Method for manufacturing a steel strip or sheet consisting mainly of Mn-austenite Download PDF

Info

Publication number
TW522060B
TW522060B TW090123064A TW90123064A TW522060B TW 522060 B TW522060 B TW 522060B TW 090123064 A TW090123064 A TW 090123064A TW 90123064 A TW90123064 A TW 90123064A TW 522060 B TW522060 B TW 522060B
Authority
TW
Taiwan
Prior art keywords
steel
patent application
scope
max
strip
Prior art date
Application number
TW090123064A
Other languages
Chinese (zh)
Inventor
Gabriele Brueckner
Wolfgang Schlump
Hans-Joachim Krautschick
Original Assignee
Krupp Thyssen Nirosta Gmbh
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Krupp Thyssen Nirosta Gmbh filed Critical Krupp Thyssen Nirosta Gmbh
Application granted granted Critical
Publication of TW522060B publication Critical patent/TW522060B/en

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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

Abstract

The method according to the invention can be used for the economic manufacture of a steel strip (W) or sheet consisting mainly of Mn-austenite which possesses enhanced strength compared with the prior art. For this purpose a steel is melted which contains at least the following alloying components (in wt. %), 15.00-24.00% Cr, 5.00-12.00% Mn, 0.10-0.60% N, 0.01-0.2% C, max. 3.00% Al and/or Si, max. 0.07% P, max. 0.05% S, max. 0.5% Nb, max. 0.5% V, max. 3.0% Ni, max. 5.0% Mo, max. 2.0% Cu as well as iron and unavoidable impurities as the remainder. This steel is cast into a thin strip (D) having a maximum thickness of 10 mm in a casting gap formed between two rotating rollers (2, 3) or rolls. The rollers (2, 3) or rolls are cooled so intensively that the thin strip (D) in the casting gap (4) is cooled at a cooling rate of at least 200 K/s. The single figure is intended for the summary. Method for manufacturing a steel strip (W) or sheet consisting mainly of Mn-austenite, in which a steel is melted which contains the following alloying constituents (in wt. %): 15.00-24.00% Cr, 5.00-12.00% Mn, 0.10-0.60% N, 0.01-0.2% C, max. 3.00% Al and/or Si, max. 0.07% P, max. 0.05% S, max. 0.5% Nb, max. 0.5% V, max. 3.0% Ni, max. 5.0% Mo, max. 2.0% Cu, and iron and unavoidable impurities as the remainder, and in which the steel is cast in a casting gap formed between two rotating rollers (2, 3) or rolls into a thin strip (D) having a maximum thickness of 10 mm, whereby the rollers (2, 3) or rolls are cooled so intensively that the thin strip (D) in the casting gap (4) is cooled at a cooling rate of at least 200 K/s.

Description

522060 A7 B7 五、發明説明（1 ) 本發明係關於一種製造主要由錳-沃斯田體組成的帶 鋼或薄鋼板。適合用於製造此等產品鋼被標示為AISI 200 且帶有編號S20100至S24000。此類型鋼材料與其它材料 之差異為具有高強度，甚至於熔接後於熔接縫區仍然保有 南強度。 此種良好強度性質係經由間隙及取代型混合晶體硬 化達成。碳及氮用於此種方面特別有用。但也可能形成非 期望的碳化物，故須避免較高碳含量。如此，但偏好用於 此種類型鋼的間隙型混合晶體硬化。但具有較高氮含量之 鋼的製造於合金化成分或製造需要的裝置而言相當昂貴。 於較高氮含量鋼之已知製法中，炫鋼係於施加壓縮 負載下熔化。此種情況下施加於熔鋼的壓力遠高於適當鋼 内氮氣成為溶液的氮分壓。此種程序之優點為可製造含較 高氮含量之鋼而無需添加特定量的其它合金化組成分。但 其缺點為所需設備高度昂貴。 另一種於熔化過程藉施加壓縮負載而溶解氮之方法 涉及提高熔鋼本身的溶解度。此項目的可藉高鉻及錳含量 達成。具有對應組成之鋼之性質說明由M. du Toit匯編， 目前可查詢「www.tecnet.co.za/mags/steel/featurel.htm」。 已知鋼可以習知方式熔化及鑄造而無需施用任何壓縮負 載，但無法用於連續鑄造。如此已知鋼的禱造成本高。 前述類型可以習知方式鑄造的鋼強度進一步提升， 可經由與鋁及/或矽合金化達成。此二元素支援混合晶體 硬化，如此導致強度的進一步提升。此外添加鋁及矽可能 本紙張尺度適用中國國家標準（CNS) A4規格（210X297公釐） 4 -------------------------------------、可............-1 線· (請先閲讀背面之注意事項再填寫本頁) 522060522060 A7 B7 V. Description of the invention (1) The present invention relates to the manufacture of a strip or thin steel plate mainly composed of manganese-voss field. Suitable steels for these products are designated AISI 200 and numbered S20100 to S24000. The difference between this type of steel material and other materials is that it has high strength, and even after welding, it still retains the southern strength in the weld seam area. Such good strength properties are achieved through hardening of interstitial and substituted mixed crystals. Carbon and nitrogen are particularly useful for this purpose. However, undesired carbides can also be formed, so higher carbon content must be avoided. This is the case, but interstitial mixed crystal hardening is preferred for this type of steel. However, steels with higher nitrogen content are relatively expensive to manufacture with alloying components or the equipment required to manufacture them. In the known method of producing higher nitrogen steels, dazzling steels are melted under a compressive load. In this case, the pressure applied to the molten steel is much higher than the nitrogen partial pressure of the nitrogen in the solution to the proper steel. The advantage of this procedure is that steels with higher nitrogen content can be manufactured without the need to add specific amounts of other alloying components. However, it has the disadvantage that the required equipment is highly expensive. Another method to dissolve nitrogen by applying a compressive load during the melting process involves increasing the solubility of the molten steel itself. This project can be achieved with high chromium and manganese content. The description of the properties of the steel with the corresponding composition is compiled by M. du Toit, and currently available at "www.tecnet.co.za/mags/steel/featurel.htm". It is known that steel can be melted and cast in a conventional manner without applying any compressive load, but cannot be used for continuous casting. The prayer of steel is thus known to result in a high cost. The strength of the aforementioned types of steels that can be cast in a conventional manner can be further improved by alloying with aluminum and / or silicon. These two elements support the hardening of the mixed crystal, which leads to a further increase in strength. In addition, the addition of aluminum and silicon may be applicable to the Chinese National Standard (CNS) A4 specification (210X297 mm) at this paper size. 4 -------------------------- ----------- 、 may ............- 1 line · (Please read the precautions on the back before filling this page) 522060

、發明説明 響堆疊錯誤能，而又再度影響變形過程。 如此添加鋁，導致堆疊錯誤能的增高，而有助於藉矿 =變形。㈣可降低堆疊錯誤能，卻有利於藉形二 田政體而變形。由於組合添加矽及鋁的結果，變形過程中 材料的強化特別受影響。麻田散體變形結果導致高产強化 而該強化因形成孿晶而降低。 添加鋁及矽至所述類型鋼的優點被其缺點抵消，缺點 為其為鐵氧體生成劑，％此有利於—次鐵氧體硬化。結果 形成的鐵氧體對氮的溶解度低。 結果於硬化過程中氮氣以氣泡形式消失。為了達成言 強度沃斯田體鋼而仍然保有較高氮含量，須將沃斯田體= 定化。如此要求進-步提高齡量，除了提高原料成本: 外也造成如此高鏟鋼於鋼加工時的製造問題。 同 ·:.!...................裝…： (請先閲讀背面之注意事項再填窝本頁) 、訂— :線丨 如此有待藉本發明解決之問題係提供一種主要為猛_ 沃斯田體組成的鋼之製造方法，該種鋼可經濟地製造且 時比較先前技藝具有較高強度。 該項問題可藉一種方法解決，該種製造主要由錳-沃斯 田體組成的帶鋼或薄鋼板之方法，其中鋼被熔化，鋼含有 下列合金化組成（以重量百分比表示）： 15.00- 24.00 % 鉻， 5.00- 12.00 % 錳， 0.10-0.60 % 氮， 0.01-0.2 % 碳， 最大值3·00 %鋁及/或矽， 太紙張尺麼摘用中國國定燋準iCNS) Α4规格（210X297公努） 522060 A7 _____B7_ 五、發明説明（3 ) 最大值0.07 %填， 最大值0.05 %硫， 最大值0.5 %鈮， 最大值0.5 %釩， 最大值3.0 %鎳， 最大值5.0 % _， 最大值2.0 %銅， 以及鐵及無可避免的雜質作為差額， 以及其中鋼係於兩根旋轉輥軸或輥形成鑄造的間隙 間被鑄造成具有最大厚度10毫米的薄帶鋼，藉此方式輥軸 或輥被強力冷卻，讓鑄造間隙的薄帶鋼係以至少200度K/ 秒之冷卻速率冷卻。薄帶鋼厚度較佳為1至5毫米。當然， 根據本發明使用的鋼組成細節也包括合金化元素含量為零 的此種成分，對其僅列舉含量的最大容許上限。 根據本發明之進一步細節，鋼之鉻含量限於 17.00-21.00重量％鉻，锰含量限於8,〇〇-12.〇〇重量％鐘及/ 或氮含量限於0.40-0.60重量％氮。此外鎳、鉬及/或銅含量 可存在於鋼。 含於本發明使用之鋼組合物之合金化元素含量於各 個案例可就元素的作用調整為最理想化。如此鉻、猛、鋼、 釩、鈮及鋁提高氮於熔鋼的溶解度，而鎳及銅屬於沃斯田 體生成劑，矽降低氮溶解度。如所述，矽也作為混合晶體 硬化劑。此外可用於晶粒的精製以及降低堆疊錯誤能。它 方面，鋁可提高堆疊錯誤能。鉬也作為混合晶體硬化劑， 本紙張尺度適用中國國家標準（⑽）A4規格（21〇><297公复） .........:…•袭---------………-訂-------------_緣 (請先閲讀背面之注意事項再填寫本頁) 522060 A7 _；____ B7 五、發明説明（4 ) 改良防姓性。釩也具有晶粒精製作用並提高強度。添加鈮 藉由促成硬化而提升強度。 本發明使用帶鋼鑄造廠基本上已知技術，鋼係於例 如雙滾軸鑄造裝置的滾軸或輥間形成的鑄造間隙鑄造，以 及被強力冷卻，因此由一次鐵氧體硬化朝向一次沃斯田體 硬化遷移。如此，由於沃斯田體具有氮之高溶解度，故可 將溶解於熔鋼之氮轉入鋼。此種強力冷卻唯有下述方式才 可能達成，經由於鑄造間隙鑄造薄帶鋼，鑄造間隙之由鑄 造輥或滾軸形成的側壁係以與鑄造帶鋼大致等速的速度移 動，因而確保側壁（鑄造輥/滾軸）與鎊造帶鋼於鎢造間隙 連續徹底進行熱交換。 徹底冷卻係以高冷卻速率進行，確保於硬化後炼鋼 可此形成的氮氣氣泡維持小氣泡，且朝向該等氣泡之壓力 大。如此避免任何氮氣於硬化過程中溢出。此外，此種氮 氣的逃逸也可藉高鐵靜力壓壓抑，高鐵靜力壓係由於於錄 .造間隙溶鋼池高度高所產生。藉此方式可確保任何形成氮 氣氣泡的壓力PN經常性低於周圍壓力Pa，鐵靜力壓以及 氣泡表面張力σ相對於氣泡半徑Γ兩倍之和（換言之 Pn<Pa+Pf+2 or /r) 〇 特別於本發明使用之該類型鋼而言，於帶鋼錄造過 程中’鑄造帶鋼的快速硬化而抵消鋼組成選擇上的高度自 由度的優點。如前文說明，由於快速硬化結果可能溶解較 大量氮氣。如此，可改良材料性質的合金化元素可比較先 刖製法以更大量添加，但未考慮及合金化元素可能對氮氣 本纸張尺度適用中國國家標準（CNS) A4規格（210父297公爱） 522060 A7 — _______Β7 五、發明説明（5 ) (請先閲讀背面之注意事項再填寫本頁) /谷解度的負面影響。例如若鋼含較大量石夕，則由於緩慢硬 化結果造成習知製造時的氮氣逃逸以及關聯的鐵氧體形成 增加的風險可於本發明方法予以消除。又於鋁含量提高案 例，於較緩慢冷卻過程中形成氮化鋁可根據本發明提供快 速冷卻予以避免。如此無需顧慮因緩慢冷卻造成的有害影 響，本發明允許使用之鉻合金的變形機轉特別經由適當選 擇鋁及矽含量調整’因而獲得具有最理想性質的終產物。 根據本發明使用之該類型鋼本質上難以變形，而加 工本發明鋼所達成的成本效益相當顯著。如此可應用至含 7.5重量％猛可藉習知連續鑄造法鑄造的鋼，也適用於含 超過7.5重量％錳無法藉習知方塊鑄造法鑄造的鋼，後述 鋼塊隨後若有所需藉通過製成數次而被滾軋成為預定最終 厚度。 目前由可連續鑄造合金製成的熱帶鋼僅可於習知熱 I帶軋機製造成最小厚度3.5毫米。具有目標厚度0.8-1.2 毫米的冷帶鋼製造唯有藉中間退火才能達成。於涉及根據 本發明之鑄造帶鋼之方法中，由於獲得的熱帶鋼厚度較小 故不再需要中間退火。因藉本發明提供之鑄造帶鋼可生產 最終厚度1至3毫米的薄帶鋼，故於多種情況下，也可調整 所製造帶鋼之最終厚度，因而可完全免除冷軋。藉此方式， 可避免於習知製造方法中由於猛_沃斯田體之變形能力低 所引發的問題。 根據本發明方法可用於製造具有特高氮含量〇.4至〇.6 重量％且合金化高達3 〇/❶鋁及/或矽之帶鋼及薄鋼板，而無 本紙張尺度朝巾關緖準Γσ«ΓΑ4胁（210X297公釐)~^ 522060 A7 B7 五、發明説明（6 ) 需於過高壓力下製造鋼或無需特高錳含量。如此製造的鋼 品具有細小晶粒各向同性結構帶有略微巨觀分離或有少數 粗粒包含體。此種鋼品由於其鋁及/或矽含量的結果，比 較先前技藝鋼品也具有較高強度及延展性。用於根據本發 明製造的帶鋼或薄鋼板，於變形過程中的強化以及能量吸 收可特別經由選擇合金而調整。 薄帶鋼的製造較佳係於保護性氣氛下進行。由於於 保濩性氣氛下鑄造結果，容易製造具有經修改表面的薄帶 鋼，而其氧化程度特別受影響。藉此方式，可避免氧化皮 的形成。 如此製造的帶鋼隨後可於輥座台上「線上」熱軋而 無滚軸沾黏的風險。若於熱軋前薄帶鋼被加熱至初滾軋溫 度時此種特性尤其優異。由於溫度增高結果，於熱滾軋過 程可達成更高度變形。 於熱滾軋後經由讓熱帶鋼接受加熱處理，特別可讓 其結構變得最理想化。加熱處理包含退火接著為以控制方 式冷卻。 根據本發明製造的薄鋼板由於其性質，故特別適人 應用於製造汽車車體鋼板金屬部件，加勁結構組件特別用 於一般交通工具的建造，特別汽車的製造、起落架或底盤 部件、車輪及油箱。所有此等應用用途中，根據本發明方 法製造的薄鋼板具有特別良好強度性質因而產生有利效 果。此外，根據本發明之薄鋼板及帶鋼具有良好防餘性可 應用於接觸活潑介質例如燃料的用途。 (請先閲讀背面之注意事項再填寫本頁) •裝· 、可丨 :線丨 9 . 522060 A7 B7 五、發明説明（8 於滾軋機7熱滾軋後，熱帶鋼w於連續退火爐8退火， 以及然後於冷卻裝置9以經過控制之方式冷卻俾特別改良 其結構。然後如此經加熱處理後的熱帶鋼w經捲取而形成 鋼卷10。 以鈾文說明方式製造的帶鋼由於介於雙滾軸鑄造裝 置的滾軸2與3間快速冷卻而達成高氮含量結果，比具有習 知組成且藉習知方法鑄造的帶鋼，具有特高強度伴隨有良 好變形性以及同等優異的能量吸收性質。2. Description of the invention It affects the stacking error energy, and once again affects the deformation process. Adding aluminum in this way leads to an increase in stacking error energy, which helps to borrow ore = deformation. Can reduce the stacking error energy, but is conducive to the deformation of the shape of Ertian regime. As a result of the combined addition of silicon and aluminum, the strengthening of the material during deformation is particularly affected. As a result of deformation of the Mata loose body, high-yield strengthening is achieved, which is reduced by the formation of twins. The advantages of adding aluminum and silicon to said types of steel are offset by their disadvantages, which are ferrite generators, which is beneficial for secondary ferrite hardening. As a result, the formed ferrite has a low solubility in nitrogen. As a result, nitrogen gas disappeared as a bubble during the hardening process. In order to reach the strength of the Vostfield body steel and still maintain a high nitrogen content, the Vostfield body must be fixed. This requires a further increase in age, in addition to increasing raw material costs: it also causes such high manufacturing problems in steel processing. Same as ::! ......... install ...: (Please read the precautions on the back before filling in this page), order —: line 丨 so to be borrowed The problem to be solved by the present invention is to provide a method for manufacturing steel mainly composed of voodoo fields, which can be economically manufactured and has higher strength than the prior art. This problem can be solved by a method of manufacturing a strip steel or a thin steel plate mainly composed of a manganese-voss field, in which the steel is melted and the steel contains the following alloying composition (expressed in weight percentage): 15.00- 24.00% chromium, 5.00- 12.00% manganese, 0.10-0.60% nitrogen, 0.01-0.2% carbon, maximum 3.00% aluminum and / or silicon, too large paper ruler, use Chinese national standard iCNS) Α4 size (210X297 (Gong Nu) 522060 A7 _____B7_ V. Description of the invention (3) Maximum 0.07% fill, maximum 0.05% sulfur, maximum 0.5% niobium, maximum 0.5% vanadium, maximum 3.0% nickel, maximum 5.0% _, maximum The value 2.0% copper, and iron and unavoidable impurities as the difference, and the steel is cast into a thin strip steel with a maximum thickness of 10 mm between the two rotating rollers or the gap formed by the casting. The shaft or roller is strongly cooled, so that the thin strip steel in the casting gap is cooled at a cooling rate of at least 200 degrees K / s. The thickness of the thin strip steel is preferably 1 to 5 mm. Of course, the details of the composition of the steel used according to the present invention also include such components with zero alloying element content, for which only the maximum allowable upper limit of the content is enumerated. According to further details of the invention, the chromium content of the steel is limited to 17.00-21.00% by weight chromium, the manganese content is limited to 8,000-12.00% by weight and / or the nitrogen content is limited to 0.40-0.60% by weight nitrogen. In addition nickel, molybdenum and / or copper content may be present in the steel. The content of the alloying elements contained in the steel composition used in the present invention can be optimized in each case with respect to the effect of the elements. In this way, chromium, manganese, steel, vanadium, niobium and aluminum increase the solubility of nitrogen in molten steel, while nickel and copper belong to the Voss field generator, and silicon reduces the solubility of nitrogen. As mentioned, silicon also acts as a mixed crystal hardener. In addition, it can be used for crystal refining and reducing stack error. For its part, aluminum improves stack error performance. Molybdenum is also used as a mixed crystal hardener. The paper size is applicable to Chinese national standard (⑽) A4 specification (21〇 > < 297 public reply) .........: ... --- ……… -Order -------------_ Yuan (Please read the notes on the back before filling this page) 522060 A7 _; ____ B7 V. Description of the invention (4) Improvement Anti-surname. Vanadium is also used for grain refinement and improves strength. Adding niobium increases strength by promoting hardening. The present invention uses a technique basically known in a strip foundry, in which steel is cast in, for example, a casting gap formed between rollers or rolls of a double-roller casting device, and is strongly cooled, so it is hardened from one ferrite to one Field hardening and migration. In this way, since the Voss field has a high solubility of nitrogen, the nitrogen dissolved in the molten steel can be transferred to the steel. Such strong cooling can only be achieved by casting thin strips through the casting gap. The side walls formed by the casting rolls or rollers in the casting gap are moved at approximately the same speed as the casting strip, thus ensuring the side walls. (Cast roll / roller) Continuous and complete heat exchange with the tungsten steel strip in the tungsten steel gap. Thorough cooling is performed at a high cooling rate to ensure that the nitrogen bubbles formed by the steelmaking after hardening can maintain small bubbles, and the pressure towards these bubbles is high. This prevents any nitrogen from escaping during the hardening process. In addition, the escape of this nitrogen gas can also be suppressed by the high pressure of the static pressure of the high-speed rail, which is caused by the high height of the molten steel pool in the recording gap. In this way, it can be ensured that the pressure PN of any nitrogen bubble formation is always lower than the surrounding pressure Pa, the static pressure of iron and the surface tension of the bubble σ with respect to the sum of the bubble radius Γ twice (in other words, Pn < Pa + Pf + 2 or / r ) 〇 Especially for the type of steel used in the present invention, the rapid hardening of the cast strip during the strip recording process offsets the advantage of a high degree of freedom in steel composition selection. As explained earlier, a relatively large amount of nitrogen may be dissolved as a result of rapid hardening. In this way, the alloying elements that can improve the material properties can be added in a larger amount than the previous method, but the alloying elements are not considered and the alloying elements may be applied to the Chinese National Standard (CNS) A4 specification for the paper size (210 parent 297 public love) 522060 A7 — _______ Β7 V. Description of the invention (5) (Please read the precautions on the back before filling out this page) / Negative effect of Gujiedu. For example, if the steel contains a large amount of stone, the risk of nitrogen escape during conventional manufacturing and the associated increase in ferrite formation due to slow hardening results can be eliminated by the method of the present invention. In the case where the aluminum content is increased, the formation of aluminum nitride during the slower cooling process can be avoided by providing rapid cooling according to the present invention. In this way, there is no need to worry about the harmful effects caused by the slow cooling. The deforming machine of the chromium alloy allowed by the present invention is specially adjusted by appropriately selecting the aluminum and silicon content, thereby obtaining the final product with the most ideal properties. The type of steel used according to the invention is inherently difficult to deform, and the cost-effectiveness achieved by processing the steel of the invention is quite significant. In this way, it can be applied to steels containing 7.5% by weight that can be cast by the conventional continuous casting method. It can also be applied to steels that contain more than 7.5% by weight of manganese that cannot be cast by the conventional block casting method. Rolled several times to a predetermined final thickness. Currently, hot-rolled steel made of continuously cast alloys can only be made to a minimum thickness of 3.5 mm by the conventional hot-rolling mechanism. Cold strip steel with a target thickness of 0.8-1.2 mm can only be achieved by intermediate annealing. In the method involving casting a steel strip according to the present invention, since the obtained hot-rolled steel has a small thickness, intermediate annealing is no longer required. Since the cast strip provided by the present invention can produce a thin strip with a final thickness of 1 to 3 mm, the final thickness of the manufactured strip can also be adjusted in many cases, thereby completely eliminating cold rolling. In this way, the problems caused by the low deformation capacity of the fierce vortex field in the conventional manufacturing method can be avoided. The method according to the present invention can be used to produce strip steel and sheet steel with extremely high nitrogen content of 0.4 to 0.6% by weight and alloying up to 30 / ❶aluminum and / or silicon, without the paper size of the paper. Quasi Γσ «ΓΑ4 threat (210X297 mm) ~ ^ 522060 A7 B7 V. Description of the invention (6) It is necessary to manufacture steel at excessively high pressure or no extra high manganese content is required. The steel thus produced has a fine-grained isotropic structure with slightly macroscopic separation or a few coarse-grained inclusions. As a result of this aluminum and / or silicon content, this type of steel also has higher strength and ductility than prior art steel products. The strength and energy absorption of the strip or thin steel sheet used in the manufacture of the present invention during deformation can be adjusted in particular through the selection of the alloy. The production of the thin strip steel is preferably performed in a protective atmosphere. As a result of casting in a protective atmosphere, it is easy to manufacture thin strips with modified surfaces, and the degree of oxidation is particularly affected. In this way, the formation of scale can be avoided. The strip thus manufactured can then be hot rolled "on-line" on the roller table without the risk of sticking the rollers. This characteristic is particularly excellent if the thin strip is heated to the initial rolling temperature before hot rolling. As a result of the increased temperature, a higher degree of deformation can be achieved during the hot rolling process. The hot-rolled steel is subjected to heat treatment after hot rolling, which can particularly optimize its structure. The heat treatment includes annealing followed by cooling in a controlled manner. Due to its properties, the thin steel plate manufactured according to the present invention is particularly suitable for the manufacture of steel sheet metal parts for automobile bodies. The stiffened structural components are particularly suitable for the construction of general vehicles, the manufacture of special automobiles, landing gear or chassis components, wheels, and tank. In all of these applications, the thin steel sheet produced according to the method of the present invention has particularly good strength properties and thus produces advantageous effects. In addition, the thin steel sheet and strip steel according to the present invention have good residual resistance and can be applied to applications in contact with a live medium such as fuel. (Please read the precautions on the back before filling in this page) • Installation ·, OK 丨: Line 丨 9. 522060 A7 B7 V. Description of the invention (8 After hot rolling in the rolling mill 7, hot-steel steel in continuous annealing furnace 8 Annealing, and then cooling in a controlled manner in a cooling device 9 to particularly improve its structure. Then the heat-treated tropical steel w is coiled to form a steel coil 10. The strip steel manufactured by the uranium description method is Fast cooling between the rollers 2 and 3 of the double-roller casting device to achieve a high nitrogen content result. Compared with a strip with a known composition and cast by conventional methods, it has extra high strength with good deformability and equally excellent Energy absorption properties.

下表比較於根據本發明之鑄造工廠1製造的熱帶鋼W 之優異強度值與習知藉連續鑄造而製造的錳沃斯田體鋼之 強度值。 (請先·閲讀背面之注意事項再填窝本頁) •訂—The following table compares the superior strength values of the tropical steel W manufactured by the foundry 1 according to the present invention with the strength values of conventional manganese Vostian body steel manufactured by continuous casting. (Please read the notes on the back before filling in this page)

Rp〇.2 Rm A80 [MPa] 「MPa] [%] 本發明 550-650 850-900 35-45 習知 420 750-800 50 :線丨 本紙張尺度適用中國國家標準（CNS) A4規格（210X297公釐） 522060 A7 B7 五、發明説明（9 ) 1.. .鑄造滾軸工廠 2，3…滾軸 4…鑄造間隙 5…爐6.. .殼體7.. .滾軋機 元件標號對照 8.. .連續退火爐 9.. .冷卻裝置 10…捲軸 D...薄帶鋼 W...熱帶鋼 5.. .溶鋼池 (請先閲讀背面之注意事項再填寫本頁) 本紙張尺度適用中國國家標準（CNS) A4規格（210X297公釐） 12Rp〇.2 Rm A80 [MPa] "MPa] [%] The present invention 550-650 850-900 35-45 Custom 420 750-800 50: Line 丨 This paper size applies Chinese National Standard (CNS) A4 specification (210X297 (Mm) 522060 A7 B7 V. Description of the invention (9) 1 ... Casting roller factory 2, 3 ... Roller 4 ... Casting gap 5 ... Furnace 6 .... Housing 7. Rolling mill component number comparison 8 .. Continuous Annealing Furnace 9. Cooling Device 10 ... Reel D ... Strip Steel W ... Tropical Steel 5 .. Melting Steel Pool (Please read the precautions on the back before filling this page) Applicable to China National Standard (CNS) A4 specification (210X297 mm) 12

Claims (1)

522060 A B c D Q Η HI 卒522060 A B c D Q Η HI 六、申I青專利範圍 第9〇123〇64號專利申請案申請專利範圍修正本91年06月26曰 1· 一種製造主要由猛·'沃斯田體組成的帶鋼 (w)或薄鋼板之方法， -其中鋼經熔化而鋼含有下列合金化成分（以重量百 分比表示）·· 15.00- 24.00 % 鉻， 5.00- 12.00 % 錳， 0.10-0.60 % 氮， 0.01-0.2 % 碳， 裝 最大值3.00 %鋁及/或矽， 最大值0.07 %磷， 最大值0·05 %硫， 最大值0 · 5 %銳， 訂 最大值0.5 %飢， 最大值3.0 %錄， 最大值5.0 %鉬， 最大值2.0 %銅， 以及鐵和無可避免的雜質為差額， 以及 -其中鋼係於兩根旋轉輥軸（2，3)或輥形成的鑄造 間隙間被鑄造成具有最大厚度為1〇毫米的薄帶鋼⑴）， 随後輥軸（2，3)或輥被強力冷卻，讓鑄造間隙4的薄帶 鋼（D)係以至少2〇〇度K/秒之冷卻速率冷卻。 2. 如申請專利範圍第1項之方法，其中薄帶鋼 (D)之厚度為1至5亳米。 3· 如申請專利範圍第1或2項之方法，其中鋼 T本紙張尺度適用甲國國家群（CNS)又_4規格（21〇X297&^_)_ 13 522060 六、申請專利範圍 含有17.〇〇_21.〇0重量％鉻Q 4· 如申請專利範圍第1項之方法，其中鋼含有 8 〇〇_12·00 重量 〇/〇錳。 5· 如申請專利範圍第1項之方法，其中鋼含有 〇·40_0·60 重量 ％氮。 6. 如申請專利範圍第1項之方法，其中該鋼額 外含有鎳、鉬及/或銅。 7 · 如申請專利範圍第1項之方法，其中薄帶鋼 (D)之鑄造係於保護性氣體氣氛下進行。 8· 如申請專利範圍第1項之方法，其中於鑄造 後，薄帶鋼（D)經連續熱滾軋而獲得熱帶鋼（w)。 a 9·★如申請專利範圍第8項之方法，其中於熱滚 軋别，薄帶鋼（D)經加熱至初滾軋溫度。 1〇·如申請專利範圍第9項之方法，其中加熱係 於保護性氣體下進行。 ,u.如申請專利範圍第8項之方法，其中於熱滚 軋後，熱帶鋼（W)接受加熱處理。 " 12. 一種由如申請專利範圍第1至11項中任一項 之方法製造之帶鋼，其係用作為汽車車體板形金屬部件 材料。 τ 13. —種由如申請專利範圍第1至11項中任—項 之方法製造之帶鋼，其係用作為加勁結構組件材料。、 14. —種由如申請專利範圍第1至U項中任—項 之方法製造二鋼’其係用作為起落架或底盤部件材 本紙張尺度適用中國國家辟（c^^ii7TIQX297公^ 522060 A B c D 申請妒範圍 15. 一種由如申請專利範圍第1至11項中任一項 之方法製造之帶鋼，其係用作為車輪材料。 16. —種由如申請專利範圍第1至11項中任一項 之方法製造之帶鋼，其係用作為油箱材料。 本紙張尺度適用中國國家標準（CMS) A4規格（210X297公釐） 15Sixth, apply for the scope of patent application No. 9123123 patent application amendment scope of the patent application June 26, 91 1 · a kind of strip steel (w) or thin Method of steel plate,-where the steel is melted and the steel contains the following alloying components (expressed in weight percentage) ... 15.00-24.00% chromium, 5.00-12.00% manganese, 0.10-0.60% nitrogen, 0.01-0.2% carbon, maximum loading The value is 3.00% aluminum and / or silicon, the maximum value is 0.07% phosphorus, the maximum value is 0.05% sulfur, the maximum value is 0.5% sharp, the maximum value is 0.5%, the maximum value is 3.0%, the maximum value is 5.0% molybdenum, The maximum is 2.0% copper, and the difference between iron and unavoidable impurities, and-where the steel is cast between two rotating roller shafts (2, 3) or the casting gap formed by the rollers has a maximum thickness of 10 mm Then, the roll shaft (2, 3) or the roll is strongly cooled, and the thin strip (D) of the casting gap 4 is cooled at a cooling rate of at least 200 degrees K / s. 2. The method according to item 1 of the patent application scope, wherein the thickness of the thin strip steel (D) is 1 to 5 mm. 3. If the method of applying for item 1 or 2 of the scope of patent application, in which the paper size of steel T is applicable to Country Group A (CNS) and _4 specifications (21〇X297 & ^ _) _ 13 522060 6. The scope of patent application contains 17 〇〇_21.〇0% by weight of chromium Q 4 · The method according to item 1 of the scope of patent application, wherein the steel contains 8000-12. 00 weight 0 / 〇 manganese. 5. The method according to item 1 of the scope of patent application, wherein the steel contains 0.40 to 60% by weight of nitrogen. 6. The method of claim 1 in which the steel additionally contains nickel, molybdenum and / or copper. 7 · The method according to item 1 of the scope of patent application, wherein the thin strip steel (D) is cast in a protective gas atmosphere. 8. The method according to item 1 of the scope of patent application, wherein after casting, the thin strip steel (D) is continuously hot-rolled to obtain the hot strip steel (w). a 9 · ★ The method according to item 8 of the scope of patent application, wherein in the hot rolling, the thin strip steel (D) is heated to the initial rolling temperature. 10. The method according to item 9 of the patent application, wherein the heating is performed under a protective gas. u. The method according to item 8 of the scope of patent application, wherein the hot-rolled steel (W) is subjected to heat treatment after hot rolling. " 12. A strip manufactured by a method according to any one of claims 1 to 11 for use as a material for a plate-shaped metal part of a car body. τ 13. A strip manufactured by a method such as any one of claims 1 to 11 of the scope of patent application, which is used as a material for stiffening structural components. 14, 14. A method for manufacturing Ergang by the method of any of the items 1 to U in the scope of the patent application, which is used as a landing gear or chassis component material. The paper size is applicable to the Chinese national standard (c ^^ ii7TIQX297 public ^ 522060 AB c D Application scope 15. A steel strip manufactured by a method such as any one of claims 1 to 11 for use as a wheel material. 16. —A category such as from claims 1 to 11 The steel strip manufactured by the method of any one of the above items is used as the fuel tank material. This paper size is applicable to the Chinese National Standard (CMS) A4 specification (210X297 mm) 15
TW090123064A 2000-09-19 2001-09-19 Method for manufacturing a steel strip or sheet consisting mainly of Mn-austenite TW522060B (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
DE10046181A DE10046181C2 (en) 2000-09-19 2000-09-19 Process for producing a steel strip or sheet consisting predominantly of Mn austenite

Publications (1)

Publication Number Publication Date
TW522060B true TW522060B (en) 2003-03-01

Family

ID=7656678

Family Applications (1)

Application Number Title Priority Date Filing Date
TW090123064A TW522060B (en) 2000-09-19 2001-09-19 Method for manufacturing a steel strip or sheet consisting mainly of Mn-austenite

Country Status (12)

Country Link
US (1) US20040025979A1 (en)
EP (1) EP1319091B1 (en)
JP (1) JP2004509762A (en)
KR (1) KR100748256B1 (en)
CN (1) CN100357478C (en)
AT (1) ATE350504T1 (en)
AU (1) AU2002210506A1 (en)
BR (1) BR0113950A (en)
DE (2) DE10046181C2 (en)
ES (1) ES2279831T3 (en)
TW (1) TW522060B (en)
WO (1) WO2002024969A1 (en)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
TWI392749B (en) * 2009-12-17 2013-04-11 Ind Tech Res Inst Easy rolling alloy material

Families Citing this family (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7485196B2 (en) * 2001-09-14 2009-02-03 Nucor Corporation Steel product with a high austenite grain coarsening temperature
AT501044B8 (en) * 2004-10-29 2007-02-15 Voest Alpine Ind Anlagen METHOD FOR PRODUCING A CAST STEEL STRIP
AT504782B1 (en) * 2005-11-09 2008-08-15 Siemens Vai Metals Tech Gmbh METHOD FOR PRODUCING A HOT-ROLLED STEEL STRIP AND COMBINED CASTING AND ROLLING MACHINE TO PERFORM THE METHOD
EP2163659B1 (en) 2008-09-11 2016-06-08 Outokumpu Nirosta GmbH Stainless steel, cold strip made of same and method for producing cold strip from same
US8182963B2 (en) * 2009-07-10 2012-05-22 GM Global Technology Operations LLC Low-cost manganese-stabilized austenitic stainless steel alloys, bipolar plates comprising the alloys, and fuel cell systems comprising the bipolar plates
CN101812646B (en) * 2010-04-22 2011-09-07 河北工业大学 High-speed steel alloy casting process used for roll
CN103614659A (en) * 2013-10-22 2014-03-05 芜湖市鸿坤汽车零部件有限公司 An austenite alloy steel material used for an internal combustion engine and a preparation method of the alloy steel material
KR101622705B1 (en) * 2014-08-06 2016-05-23 한국기계연구원 Austenite stainless steel having excellent pitting corrosion resistance
US9975170B2 (en) * 2014-12-11 2018-05-22 Posco Method for manufacturing duplex stainless steel sheet having high nitrogen content and good surface quality
DE102015005742A1 (en) 2015-05-05 2016-11-10 Dbi Gas- Und Umwelttechnik Gmbh Process for the production of sheet from a stainless, austenitic CrMnNi steel
DE102016211411A1 (en) * 2016-06-24 2017-12-28 Thyssenkrupp Ag Vehicle wheel and use
US10960487B2 (en) * 2017-09-21 2021-03-30 United States Steel Corporation Weldability improvements in advanced high strength steel
CN108179364B (en) * 2017-12-28 2019-05-31 钢铁研究总院 A kind of structural alloy steel and preparation method thereof with high impact absorption energy
CN109865806A (en) * 2018-06-08 2019-06-11 江苏沙钢集团有限公司 A kind of thin strap continuous casting 345MPa grades of weathering steels and its production method
CN110484833A (en) * 2019-08-21 2019-11-22 首钢集团有限公司 Low Mn austenitic steel of a kind of high chromium and preparation method thereof
CN111876670B (en) * 2020-06-30 2021-11-09 九牧厨卫股份有限公司 High-hardness scratch-resistant stainless steel, stainless steel water tank and preparation method thereof
CN112974532B (en) * 2021-02-05 2023-01-31 山西太钢不锈钢股份有限公司 Rolling method of ultrahigh nitrogen austenitic stainless steel hot continuous rolling coiled plate
CN115368760A (en) * 2022-07-20 2022-11-22 江苏甬金金属科技有限公司 Processing technology of antibacterial austenitic stainless steel strip
EP4316727A1 (en) 2022-08-05 2024-02-07 Outokumpu Oyj Filler metal for welding of dissimilar welds

Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2163511C3 (en) * 1971-12-21 1980-09-25 Armco Steel Corp., Middletown, Ohio (V.St.A.) Use of an austenitic ferritic stainless steel as a material for the production of cold-upset fasteners, weldments in pure chrome steels and for other applications in which magnetic steels with high ductility, good weldability and good resistance to stress cracking in chloride media are required
US4946644A (en) * 1989-03-03 1990-08-07 Baltimore Specialty Steels Corporation Austenitic stainless steel with improved castability
US5092393A (en) * 1989-03-14 1992-03-03 Nippon Steel Corporation Process for producing cold-rolled strips and sheets of austenitic stainless steel
JP2863541B2 (en) * 1989-03-29 1999-03-03 新日本製鐵株式会社 Method for producing Cr-based stainless steel sheet using thin casting method
JPH0698460B2 (en) * 1990-10-11 1994-12-07 日本冶金工業株式会社 Casting method of iron-based alloy containing Cr and Ni by twin roll type continuous casting machine
JPH06322440A (en) * 1993-05-12 1994-11-22 Nippon Steel Corp Method for rolling high manganese nonmagnetic steel slab
JPH0790471A (en) * 1993-09-17 1995-04-04 Nippon Steel Corp High mn and high n austenitic stainless steel cast slab and its production
JP3190319B2 (en) * 1994-04-04 2001-07-23 新日本製鐵株式会社 Twin roll continuous casting machine
CN1129259A (en) * 1995-07-12 1996-08-21 南京三钢(集团)股份有限公司 Nickel-chromium-saved nitrogen-contained austenite stainless steel
JPH09168844A (en) * 1995-12-19 1997-06-30 Mitsubishi Heavy Ind Ltd Twin roll continuous casting method
FR2763960B1 (en) * 1997-05-29 1999-07-16 Usinor PROCESS FOR PRODUCING FERRITIC STAINLESS STEEL THIN STRIPS AND THIN STRIPS THUS OBTAINED
IT1291931B1 (en) * 1997-06-19 1999-01-21 Voest Alpine Ind Anlagen PROCEDURE FOR THE PRODUCTION OF RAW STEEL CASTING TAPES WITH LOW CARBON CONTENT AND THIS OBTAINABLE TAPES
JP4207137B2 (en) * 1998-02-16 2009-01-14 日立金属株式会社 High hardness and high corrosion resistance stainless steel
FR2780735B1 (en) * 1998-07-02 2001-06-22 Usinor AUSTENITIC STAINLESS STEEL WITH LOW NICKEL CONTENT AND CORROSION RESISTANT
FR2783443B1 (en) * 1998-09-21 2000-10-27 Usinor PROCESS FOR THE MANUFACTURE OF A STAINLESS STEEL THIN STRIP
JP2000107803A (en) * 1998-10-07 2000-04-18 Mitsubishi Heavy Ind Ltd Manufacture of steel sheet
DE19900199A1 (en) * 1999-01-06 2000-07-13 Ralf Uebachs High strength light constructional steel for pre-stressed concrete reinforcements or automobile body components has high manganese and aluminum contents
FR2796083B1 (en) * 1999-07-07 2001-08-31 Usinor PROCESS FOR MANUFACTURING IRON-CARBON-MANGANESE ALLOY STRIPS, AND STRIPS THUS PRODUCED

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
TWI392749B (en) * 2009-12-17 2013-04-11 Ind Tech Res Inst Easy rolling alloy material

Also Published As

Publication number Publication date
JP2004509762A (en) 2004-04-02
CN1659300A (en) 2005-08-24
ES2279831T3 (en) 2007-09-01
CN100357478C (en) 2007-12-26
BR0113950A (en) 2003-07-22
DE50111818D1 (en) 2007-02-15
AU2002210506A1 (en) 2002-04-02
KR100748256B1 (en) 2007-08-10
EP1319091A1 (en) 2003-06-18
EP1319091B1 (en) 2007-01-03
ATE350504T1 (en) 2007-01-15
WO2002024969A1 (en) 2002-03-28
KR20030051660A (en) 2003-06-25
DE10046181C2 (en) 2002-08-01
US20040025979A1 (en) 2004-02-12
DE10046181A1 (en) 2002-04-04

Similar Documents

Publication Publication Date Title
TW522060B (en) Method for manufacturing a steel strip or sheet consisting mainly of Mn-austenite
JP4644076B2 (en) High strength thin steel sheet with excellent elongation and hole expansibility and manufacturing method thereof
KR940007374B1 (en) Method of manufacturing austenite stainless steel
JP2008519160A (en) Method for producing high strength steel strip or sheet having TWIP characteristics, component and method for producing high strength steel strip or sheet
JP2014520954A (en) Ultra-high strength wear-resistant steel sheet and method for producing the same
JP5005543B2 (en) High-strength thick-walled electric-welded steel pipe excellent in hardenability, hot workability and fatigue strength, and method for producing the same
KR20230059806A (en) 980 MPa class full-bainitic steel with very high hole expandability and manufacturing method thereof
KR20230059810A (en) 980MPa class bainite steel with high hole expandability and manufacturing method thereof
JP2010100877A (en) Method for manufacturing hot-rolled ferritic stainless steel sheet excellent in toughness
CN106636934A (en) Wheel steel with tensile strength being at level of 590 MPa and production method
CN102719736B (en) Steel with yield ratio of 0.9 or more used for ultra-fine grain slideway and production method thereof
CN102418047B (en) Non-quenched and tempered fatigue-resistant steel plate and manufacturing method thereof
JP2007056283A (en) High-strength thick-wall electric resistance welded steel tube having excellent hardenability and decarburization resistance, and its manufacturing method
CN114000053B (en) Hot-rolled steel sheet and method for producing same
CN110366602A (en) Thermal cycle for Austenite Grain Refinement
CN114381662A (en) Low-cost steel for pressure vessel and preparation method thereof
JPH021208B2 (en)
EP3708691B1 (en) Manufacturing method for ultrahigh-strength and high-ductility steel sheet having excellent cold formability
KR101949025B1 (en) Cold rolled steel sheet for flux cored wire and method of manufacturing the same
JP2011052243A (en) Method for manufacturing thick high-strength steel sheet superior in characteristics of stopping propagation of brittle crack
JP2019173158A (en) Steel sheet for hot stamp
CN113166896A (en) Steel material for pressure vessel having excellent hydrogen-induced cracking resistance and method for producing same
JPS5822327A (en) Production of superhigh-strength cold-rolled steel sheet by continuous annealing
TWI750033B (en) Steel plate and its manufacturing method
EP4245876A1 (en) High yield ratio and high strength steel sheet having excellent thermal stability, and manufacturing method therefor

Legal Events

Date Code Title Description
GD4A Issue of patent certificate for granted invention patent
MM4A Annulment or lapse of patent due to non-payment of fees