TW459052B - Ultra-high strength steels with excellent cryogenic temperature toughness - Google Patents

Ultra-high strength steels with excellent cryogenic temperature toughness Download PDF

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TW459052B
TW459052B TW087109691A TW87109691A TW459052B TW 459052 B TW459052 B TW 459052B TW 087109691 A TW087109691 A TW 087109691A TW 87109691 A TW87109691 A TW 87109691A TW 459052 B TW459052 B TW 459052B
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steel
temperature
weight
steel plate
iron
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TW087109691A
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Jayoung Koo
Narasimha-Rao V Bangaru
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Exxon Production Research Co
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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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Abstract

An ultra-high strength, weldable, low alloy steel, containing less than 9 wt% nickel, with excellent cryogenic temperature toughness in the base plate and in the heat affected zone (HAZ) when welded, having a tensile strength greater than 830 MPa (120 ksi) and a microstructure comprising predominantly fine-grained lath martensite and/or fine-grained lower bainite, is prepared by heating a steel slab comprising iron and specified weight percentages of some or all of the additives carbon, manganese, nickel, nitrogen, copper, chromium, molybdenum, silicon, niobium, vanadium, titanium, aluminum, and boron; reducing the slab to form plate in one or more passes in a temperature range in which austenite recrystallizes; finish rolling the plate in one or more passes in a temperature range below the austenite recrystallization temperature and above the Ar3 transformation temperature; quenching the finish rolled plate to a suitable quench stop temperature; stopping the quenching; and tempering the plate at a suitable temperature for a period of time sufficient to cause precipitation of hardening particles.

Description

經濟部中央標準局貝工消費合作社印製 f 4 c ; A7 ___ B7 五、發明説明( ) ^ 發明範圍 本發明係關於在基板及熔接後的受熱影響區域（ HA Z )都有極佳的低溫韌性之超高強度可熔接的低合金 鋼材，而且，本發明也關於此鋼材之製法。 發明背景 在下列說明中定義數個名詞，爲了方便起見，在申請 專利範圍之前，在文中提供名詞之詞彙解釋。 通常，需要在低溫也就是溫度低於約- 40 °C ( - 4 0 °F )儲存及輸送高壓的揮發性液體，例如，需要在 約 1035kPa (150psia)至約 7590 kPa (llOQpsia)的廣大壓力範圍及在約 123°C (― 1 90°F)至約一62°C (-80°F)的壓 力範圍下，供儲存及輸送高壓液態天然氣（PLNG)之 容器，同時需要安全且經濟地在低溫下供儲存及輸送高蒸 氣壓力之其他揮發性液體例如甲烷、乙烷及丙烷之容器， 對於此種經由熔接鋼材建造之容器，在操作情形下，在基 板及HA Z的鋼材都必須有適當的強度以耐受流體壓力及 適當的韌性以預防引發破裂，也就是失能事件。 延性轉脆溫度（D B TT )記述在結構鋼材上的兩種 破裂形式，在低於DBTT的溫度下，鋼材損壞容易經由 低能分解（脆裂）破裂產生，而在高於DBTT的溫度下 ，鋼材損壞容易經由高能順應性破裂產生，用於建造儲存 及輸送容器供上述低溫應用及其他荷載之熔接鋼材，低溫 本紙張尺度適用中國國家標準（CNS ) Λ4規格（210X29·；公犛） (¾先聞讀f而之注意事項孙填寫本頁〕 装. ,ιτ -4 - 經濟部中央標準局員工消費合作社印製 A7 B7 五、發明説明i ) 使用之 D B T T必須比基質鋼板及H A Z之使用溫度低很多，以 防止損壞分解破裂之損壞。 習慣使用含鎳之鋼材供低溫結構應用，例如鎳含量高 於約3重量％之鋼材，其具有低DBTT,但是也有相當 低的張力強度，逋常商業化供應之3.5重量％Ni、 5.5重量％Ni及9重量％Ni鋼材之DBTT分別爲 約一 100°C(— 150卞）、一155eC( — 250°F )及—175°C (― 280 °F),且張力強度至多分別爲 約 485Mpa (7〇ksi)、62〇Mpa (90 ks i)及 83〇Mpa (12〇fcs i)，爲了達到這 些強度與韌性之組合，這些鋼材通常進行昂貴的加工，例 如重複退火處理，在低溫應用之情形下，工業上目前使用 這些商業化供應之含鎳鋼材，因爲其在低溫下具有良好的 韌性，但是必須對其相當低的張力強度進行設計，此設計 通常需要大幅度的鋼材厚度供荷載、低溫應用，因爲鋼材 及所需鋼材厚度結合之高成本，使得這些含鎳鋼材在荷載 、低溫應用之用途傾向於昂貴。 反之，數種商業化供應之先進低量及中量碳高強度低 合金（HSLA)鋼材，例如AI S I 4320或 4 3 3 0鋼材，可提供優越的張力強度（例如大於約 830Mpa (120ks i))及低成本，但是在一般 及熔接受熱影響的特定區域（HAZ)有相當高DBTT 之問題，通常，使用這些鋼材有熔接性及低溫韌性降低而 本紙張尺度適用中國國家標準（CNS )六4说辂（210X 297公勢） (邻先閱讀背而之注意家項#填寫本頁) --e 經濟部中央標準局貝工消費合作社印聚 A7 Η 7 五、發明説明i ) 張力強度增加之傾向，基於此因素，目前商業化供應之先 進H S L A鋼材通常不考慮供低溫應用，在這些鋼材中的 HAZ之高DBTT，通常是由於在粗粒化及嚴苛重複加 熱的HAZ熔接熱區域形成不欲的微結構，也就是HAZ 加熱至從約A ^ i轉化溫度至約A。3轉化溫度，（A。i及 Ac3轉化溫度之定義參見附錄），DBTT隨著HAZ內 的粒子大小及脆變微結構成份例如麻田散鐵-沃斯田鐵（ Μ A )島狀物的增加而明顯地增大，例如在供油及氣體傳 送之X100輸送管之先進HSLA鋼材中，HAZ之 DBTT高於約一 5 0°C (― 6 0°F),發展新的鋼材使 其結合上述商業化供應含鎳鋼材之高強度且低成本 H S L A鋼材之低溫韌性，同時提供極佳的熔接性及所需 的厚部份相容性也就是在厚度大於約2 . 5公分（1吋） 處有實質上均勻的微結構及性質（例如強度及韌性），在 能量儲存及輸送領域有明顯的誘因。 在非低溫使用下，大部分商業化供應的先進低量及中 量碳HSLA鋼材，由於其在高強度下有相當低的韌性， 不是根據其強度設計就是加工成較低的強度以達到可接受 之韌性，在工程應用上，這些趨勢導致增加厚度且因此與 如果能充分利用高強度潛能之H S L A鋼材比較，有較大 的成份重量且最後有較高的成本，在某些重要的應用下， 例如高效能齒輪，使用含大於約3重量％ N i之鋼材（例 如AISI48XXX、 SAE93XX等）以維持足夠 的韌性，此方式導致達到優良強度HSL·A鋼材需要有高 本紙張尺度適用中國國家標準（CNS ) ( 2ΪΟΧ297公毋） (誚先閲讀背面之注意事項再填寫本K} 装- 丁 、ya -6- 459052 Α7 Η 7 經濟部中央標隼局員工消費合作社印製 五、發明説明4 ) 成本之代價，伴隨著使用標準商業化供應的H s L A鋼材 之其他問題是氫在H A Z中爆裂，尤其是當使用低熱輸入 熔接法。 在高及超高強度低合金鋼材中，對於低成本強化韌性 有明顯的經濟誘因及大量的工程需求，具體地說，需求一 種合理價格的鋼材，其在基板及HAZ中都具有超高強度 例如張力強度高於830Mpa (120ks i)，及極 佳的低溫韌性例如D B T T低於約一 7 3 t ( — 1 〇 〇 °F )，供在商業化低溫應用中使用。 因此，本發明之主要目的是在三個主要方面改進先進 的高強度低合金鋼材技術供在低溫下使用：（i )在基質 鋼材及熔接HAZ中，降低DBTT至低於約一 73°C ( -1 0 0 °F ) , (ii)使張力強度高於830Mpa( 120ks i)，及（i i i)提供優越的熔接性。本發 明之其他目的是達到上述的H SLA鋼材，其在厚度大於 約2 . 5公分（1吋）處之整個厚度有均勻的微結構及性 質，並可使用目前商業化存在之加工技術處理，所以使用 這些鋼材在商業化低溫處理上可以很經濟性地達成。 發明槪述 配合上述之本發明目的，提供一種處理方法其中所要 化學性之低合金鋼板塊再度加熱至適當的溫度，然後熱輥 軋形成鋼板並快速冷卻，在熱輥軋結束後，用適當的液體 例如水淬火至適當的淬火停止溫度（QST)，將鋼材之 本紙張尺度通用中國國家梯準（CNS )厶4蚬梏（210Χ29ϋ ) ("先閱讀背而之注意事項丹填寫本頁) 取- 、1Τ 459052 A7 B7 五、發明說明（5 ) 微結構轉化成主要較宜爲微細粒化條麻田散鐵、微細粒化 低變韌鐵或其混合物，然後在適當的溫度範圍下回火，在 回火化的鋼材中產生微結構，較宜主要含回火化的微細粒 化條麻田散鐵、回火化微細粒化低變韌鐵或其混合物，或 更宜實質上含1 〇 〇%回火化的微細粒化條麻田散鐵，在 本發明之說明中，使用的回火係指經由任何方法加速冷卻 ，不同於將鋼材空氣冷卻至環境溫度，其中選擇使用有增 加鋼材冷卻速率傾向之液體，在本發明之一個較佳具體實 施例中，在淬火停止及回火前，將鋼板以空氣冷卻至室溫 〇 同時，配合上述之本發明目的，根據本發明之鋼材處 理特別適用於許多低溫應用，其中鋼材具有下列特徵，較 宜爲鋼板厚度約2 . 5公分（1吋）且更大：（1 )在基 質鋼材及熔接HAZ中，DBTT低於約一 7 3°C ( ~ 1 0 0 °F ) , (ii)張力強度高於 830MPa( 120匕3 1)，較宜高於86〇^4?3(12 5 1^3 1 )，且更宜高於 900MPa (130ks i),( ill)優越的熔接性，（iv)整個厚度有實質上均勻 的微結構及性質，及（v )韌性優於標準商業化洪應的 HSLA鋼材。這些鋼材可有大於約930MPa ( 135ks i)之張力強度，或大於約965MPa ( 140ks i)，或大於約 l〇〇〇MPa (145 k s i )。 本紙張尺度適用节國國家標準（CNS)A4規格（210 X 297公釐）-8 - (請先閲讀背面之注意事項再填寫本頁) 裝- -----丨—訂--------- 經濟部智慧財產局異工消費合作社印製 經濟部中央橾準局員工消費合作社印製 A7 _ 1J7 mm .- __ _ 五、發明説明& ) 既凰之-說明 參照下列詳細說明及其中的附圖，將可更加了解本發 明之優點。 圖1 A爲根據本發明將鋼板塊再度加熱後，沃斯田鐵 粒子大小之示意圖； 圖1 B爲根據本發明，在沃斯田鐵再結晶的溫度範圍 內熱輥軋後，但在其中沃斯田鐵不會再結晶的溫度範圍內 熱輥軋前，鋼板塊中沃斯田鐵粒子大小（參見附錄）之示 意圖：且 圖1C爲完成根據本發明之TMCP後，在鋼板整個 厚度方向具有非常微細有效的粒子大小之沃斯田鐵中的長 扁平粒子結構之示意圖。 主要元件對照 10 ^ 再度加熱鋼板塊 D ^ 平均沃斯田鐵粒子大小 10" 鋼板塊 D ^ 平均先前沃斯回鐵粒子大小 10 輥軋後的鋼板 D 有效粒子大小 雖然本發明將以其較佳的具體實施例說明，必須了解 本發明並非限定於此，相反地，本發明將涵蓋可包括在本 發明精神及範圍內的全部替換、修改及相當的情形•如同 本紙張尺度適用中國國家標率《CNS ) A4規格（210X297公n ) —I；----------------ir------V ("先閱讀背而之注^^>項再填.'"本頁) -9 - Λ7 :^10 ^ 五、發明說明（7 ) 附加的申請專利範圍之定義。 "請先閱讀背面之注意事項再填寫本頁) 發明之詳細說明 本發明係關於硏發達到上述挑戰之新穎的H S L A鋼 材，本發明係基於同時提供本質及微結構強韌化，使得在 高張力強度下降低D Β Τ' T及強化韌性之鋼材化學與處理 之新穎組合，本質強軔化是經由鋼材中重要合金元素正確 判斷的平衡而達成，如同在本發明說明中之詳細敘述，微 結構強韌化源自達到非常微細有效的粒子大小以及製造微 細粒化之麻田散鐵及/或低變韌鐵條板，細小粒子之平均 大小比先前的沃斯田鐵粒子小很多，此外，在本發明麻田 散鐵/變韌鐵結構之回火過程中，可利用從銅沈澱物及混 合的碳化物/碳氮化物強化之分散性使強度及韌性最佳化 〇 經濟部智慧財產局員工消費合作社印製 根據前述說明，提供一種製備鋼板之方法，其中微結 構顯著性地含回火化的微細粒化條麻田散鐵、回火化微細 粒化低變韌鐵或其混合物，其中此方法之步驟包括（a ) 將鋼板塊在足以（1 )實質上均勻化鋼板塊，（i i )實 質上溶解鋼板塊中鈮及釩之全部的碳化物及碳氮化物，及 (1 1 i )在鋼板塊中建立微細的初沃斯田鐵粒子之溫度 下再加熱：（b )減縮鋼板塊，在沃斯田鐵再結晶的第一 個溫度範圍下，在一或多個熱輥軋通道下形成鋼板；（c )在低於約T “ ^溫度但高於約A r 3轉化溫度的第二個溫 度範圍下，在一或多個熱輥軋通道下進一步減縮鋼板；（ 本紙張尺度適用中國國家標準（CNS)A4規格（210 X 297公藿） -10- 459052 Λ7 B7 經濟部智慧財產局員工消費合作社印製 五、發明說明（8 ) d )在每秒約1 〇 t至每秒約4 0 t ( 1 8 T/秒-7 2 F/秒）之冷卻率下使鋼板淬火至低於約M s轉化溫度加 上2 〇 〇。(：（ 3 6 0 °F )之淬火停止溫度；（e )停止淬 火；及（f )在約4 0 0 t ( 7 5 2 T )至約A。I轉化溫 度之回火溫度下使鋼板回火，較宜高至但不包括A ^ i轉化 溫度足夠的時間，使沈澱硬化的粒子，也就是一或多種的ε -銅、M〇2C、或鈮及釩的碳化物及碳氮化物，足以使硬 化的粒子沈澱之時間主要決定於鋼板之厚度、鋼板之化學 、及回火溫度，並可由熟諳此藝者決定，（顯著性、硬化 粒子、T u r溫度、A r 3、Μ 、及A。i轉化溫度之定義 參見附錄）。 爲了確定室溫及低溫韌性，根據本發明之鋼材較宜主 要含回火化的微細粒化低變韌鐵、回火化微細粒化條麻田 散鐵或其混合物。較宜實質上減低脆化成份之形成例如上 變韌鐵、雙晶麻田散鐵及Μ A。在本發明之說明及申請專 利範圍中，a顯著地〃係指至少約5 0體積％，微結構更 宜含至少約6 0體積％至約8 0體積％的回火化微細粒化 低變韌鐵、回火化的微細粒化條麻田散鐵或其混合物，微 結構又更宜含至少約9 0體積％的回火化微細粒化低變韌 鐵、回火化的微細粒化條麻田散鐵或其混合物，微結構最 宜含實質上1 0 0%回火化的微細粒化條麻田散鐵。 根據本發明處理之鋼板是在習知的方式下製造，在一 個具體實施例中，含鐵及下列合金元素，較宜如下列表1 本紙張尺度適用中國國家標準（CNS)A4規格（210 χ 297公爱〉 -11 - ------------ί ^--------^---------線一 {請先閱讀背面之注意事項再填寫本頁) A7 459052 _______Η 7 五、發明説明‘) 所示之重量範圍： 表I 合金兀素 範圍（重量％) 碳（C) 0.04-0.12 ，更宜爲 0.04-0.07 猛（Μη) 0.5-2.5 , 更宜爲1.0-1.8 鎳（Ni) 1.0-3.0 , 更宜爲1.5-2.5 銅（Cu) 0.1-1.5， 更宜爲0.5-1.0 鉬（Mo) 0.1-0.8 , 更宜爲0.2-0.5 鈮（Nb) 0.02-0.1 , 更宜爲0.03-0,05 鈦（Ti) 0.008-0.03 ,更宜爲 0.0卜0,02 鋁（A1) 0.001 -0.05，更宜爲 0.005 -0.03 氮（N) 0,002-0.005，更宜爲 0.002-0.003 (許先閲讀背而之注意事項洱填寫本I)Printed by the Central Standards Bureau of the Ministry of Economic Affairs, Fung Cong Cooperative; A7 ___ B7 V. Description of the invention () ^ Scope of the invention The invention relates to the substrate and the heat-affected area (HA Z) after welding have excellent low temperature Tough, ultra-high-strength, weldable low-alloy steel, and the present invention also relates to a method for producing this steel. BACKGROUND OF THE INVENTION Several nouns are defined in the following description. For convenience, vocabulary explanations of the nouns are provided in the text before the scope of the patent application. Generally, high-pressure volatile liquids need to be stored and transported at low temperatures, that is, temperatures below about -40 ° C (-40 ° F). For example, large pressures of about 1035kPa (150psia) to about 7590kPa (110Qpsia) are required. Range and in a pressure range of about 123 ° C (-1 90 ° F) to about 62 ° C (-80 ° F), for storage and transportation of high-pressure liquid natural gas (PLNG) containers, at the same time it needs to be safe and economical Containers for storage and transportation of other volatile liquids such as methane, ethane, and propane at low temperatures. For such containers constructed by welding steel, under operating conditions, both the substrate and the HA Z steel must have Appropriate strength to withstand fluid pressure and proper toughness to prevent rupture, which is a disability event. Ductility to brittleness temperature (DB TT) describes two types of fracture on structural steels. At temperatures below DBTT, steel damage is likely to occur through low-energy decomposition (brittleness) cracking, and at temperatures above DBTT, steels Damage is easily generated by high-energy compliance cracking. It is used to build storage and transportation containers for the above-mentioned low-temperature applications and other loads of welded steel. Low-temperature paper standards are applicable to Chinese National Standards (CNS) Λ4 specifications (210X29 ·; public). After reading, please note that Sun completed this page.] Loading., Ιτ -4-Printed by the Consumers' Cooperative of the Central Standards Bureau of the Ministry of Economic Affairs A7 B7 V. Description of the invention i) The DBTT used must be lower than the temperature of the matrix steel plate and HAZ Lots of damage to prevent damage from breaking down. It is customary to use nickel-containing steels for low-temperature structural applications. For example, steels with nickel content higher than about 3% by weight have low DBTT, but also have relatively low tensile strength. 3.5% by weight of Ni and 5.5% by weight that are commonly supplied commercially The DBTT of Ni and 9% by weight Ni steel are about -100 ° C (-150 卞), -155eC (-250 ° F), and -175 ° C (-280 ° F), respectively, and the tensile strength is at most about 485Mpa, respectively. (70ksi), 62 MPa (90 ks i), and 83 MPa (120 fcs i). In order to achieve these strength and toughness combinations, these steels are usually expensively processed, such as repeated annealing, and are used at low temperatures. Under these circumstances, these commercially available nickel-containing steels are currently used in the industry because they have good toughness at low temperatures, but they must be designed with very low tensile strength. This design usually requires a large steel thickness for loading. Low temperature applications, because of the high cost of the combination of steel and required steel thickness, these nickel-containing steels tend to be expensive in load and low temperature applications. Conversely, several commercially available advanced low and medium carbon high-strength low-alloy (HSLA) steels, such as AI SI 4320 or 4 3 3 0 steels, can provide superior tensile strength (for example, greater than about 830Mpa (120ks i) ) And low cost, but there is a problem of high DBTT in general and specific heat-affected areas (HAZ). Generally, the use of these steels has reduced weldability and low-temperature toughness, and this paper size applies the Chinese National Standard (CNS). 4 Say 辂 (210X 297 public power) (Read it first and pay attention to the home item # Fill in this page) --e Printed by the Central Standards Bureau of the Ministry of Economy, Shellfish Consumer Cooperatives, A7 Η 7 V. Description of the invention i) Increased tensile strength Based on this factor, the currently commercially available advanced HSLA steels are generally not considered for low temperature applications. The high DBTT of HAZ in these steels is usually due to the formation of hot zone of HAZ welding in coarse graining and severe repeated heating. Unwanted microstructures, that is, the HAZ is heated to a temperature from about A ^ i to about A. 3 Conversion temperature, (see the appendix for the definition of A.i and Ac3 conversion temperature), the DBTT increases with the particle size and brittle microstructure components in the HAZ, such as Asada loose iron-Vostian iron (MA) islands. It is significantly increased. For example, in advanced HSLA steel for X100 pipelines for oil supply and gas transmission, the DBTT of HAZ is higher than about -50 ° C (-60 ° F). Develop new steels to combine the above. Commercial supply of high strength and low cost HSLA steels with low temperature toughness of nickel-containing steels, while providing excellent weldability and required thick part compatibility at thicknesses greater than approximately 2.5 cm (1 inch) Has a substantially uniform microstructure and properties (such as strength and toughness), and has obvious incentives in the field of energy storage and transmission. Under non-low temperature use, most of the commercially supplied advanced low and medium carbon HSLA steels, because of their relatively low toughness under high strength, are either designed according to their strength or processed to a lower strength to achieve acceptable In engineering applications, these trends lead to increased thickness and therefore higher component weights and higher costs in the end if compared to HSLA steels that can take full advantage of high strength potentials. In some important applications, For example, for high-performance gears, steels containing more than about 3% by weight of Ni (such as AISI48XXX, SAE93XX, etc.) are used to maintain sufficient toughness. This method results in high strength HSL · A steels that require high paper sizes and apply Chinese national standards ( CNS) (2Ϊ〇 × 297 公 毋) (诮 Please read the notes on the back before filling in this K} Pack-D, ya -6- 459052 Α7 Η 7 Printed by the Consumers' Cooperative of the Central Bureau of Standards of the Ministry of Economic Affairs 5. Inventory 4) Cost The price, along with the other problems associated with the use of standard commercial Hs LA steels, is hydrogen bursting in the HAZ, especially when using low heat input melts. Law. In high- and ultra-high-strength low-alloy steels, there are obvious economic incentives and a large number of engineering requirements for low-cost strengthening toughness. Specifically, a reasonable price steel is required, which has ultra-high strength in the substrate and HAZ. The tensile strength is higher than 830Mpa (120ks i), and the excellent low temperature toughness such as DBTT is lower than about 173 t (—100 ° F) for use in commercial low temperature applications. Therefore, the main objective of the present invention is to improve advanced high-strength low-alloy steel technology for use at low temperatures in three main areas: (i) In matrix steel and welded HAZ, reduce DBTT to less than about 73 ° C ( -1 0 0 ° F), (ii) make the tensile strength higher than 830Mpa (120ks i), and (iii) provide superior weldability. Another object of the present invention is to achieve the above-mentioned H SLA steel, which has a uniform microstructure and properties throughout its thickness at a thickness greater than about 2.5 cm (1 inch), and can be processed using currently existing commercial processing technologies. Therefore, the use of these steels can be economically achieved in commercial low temperature processing. Description of the invention In accordance with the above-mentioned object of the present invention, a processing method is provided in which a low-alloy steel block of desired chemical property is heated again to an appropriate temperature, and then hot rolled to form a steel sheet and rapidly cooled. After the hot rolling is completed, an appropriate Liquids such as water are quenched to the appropriate quenching stop temperature (QST), and the paper size of the steel is common to the Chinese National Standard (CNS) 厶 4 蚬 梏 (210 × 29ϋ) (" Read the precautions first and fill out this page) Take-, 1T 459052 A7 B7 V. Description of the invention (5) The microstructure is transformed into mainly fine-grained strips of Asada loose iron, fine-grained low-toughness iron or a mixture thereof, and then tempered at an appropriate temperature range. It produces microstructure in tempered steel, it is more suitable to mainly contain tempered micro-grained bar Asada loose iron, tempered micro-grained low-toughness iron or its mixture, or more preferably 100% temper In the description of the present invention, the use of tempered micro-granulated Asada loose iron refers to accelerated cooling by any method, which is different from cooling the steel air to the ambient temperature. A liquid that tends to increase the cooling rate of steel. In a preferred embodiment of the present invention, before quenching is stopped and tempered, the steel sheet is air-cooled to room temperature. At the same time, in accordance with the purpose of the present invention described above, according to the present invention The steel processing is particularly suitable for many low temperature applications. Among them, the steel has the following characteristics, which is preferably a steel plate with a thickness of about 2.5 cm (1 inch) and larger: (1) In matrix steel and welded HAZ, the DBTT is less than about one. 7 3 ° C (~ 100 ° F), (ii) tensile strength is higher than 830MPa (120 dzi 3 1), preferably higher than 86〇 ^ 4? 3 (12 5 1 ^ 3 1), and more suitable Above 900MPa (130ks i), (ill) superior weldability, (iv) substantially uniform microstructure and properties throughout the thickness, and (v) toughness superior to standard commercial HSLA steels. These steels may have a tensile strength greater than about 930 MPa (135ks i), or greater than about 965 MPa (140ks i), or greater than about 1000 MPa (145 ksi). The size of this paper is applicable to the National Standard (CNS) A4 (210 X 297 mm) -8-(Please read the precautions on the back before filling this page) ----- Printed by the Intellectual Property Bureau of the Ministry of Economic Affairs, a different consumer cooperative, printed by the Central Consumers' Bureau of the Ministry of Economic Affairs, printed by the consumer consumer cooperative of A7 _ 1J7 mm .- __ _ V. Description of the invention & The advantages of the present invention will be better understood with the description and the accompanying drawings. FIG. 1A is a schematic diagram of the particle size of Vosstian iron after the steel block is re-heated according to the present invention; FIG. 1B is a hot-rolled within the temperature range of Vosstian iron recrystallization according to the present invention. Before hot rolling in the temperature range where Stahl will not recrystallize, the schematic diagram of the particle size of Vostian iron in the steel block (see appendix): and Figure 1C is a diagram showing the thickness of the steel sheet after the completion of TMCP according to the present invention. Schematic diagram of long and flat particle structure in Vostian iron with fine and effective particle size. Comparison of main components 10 ^ reheated steel plate D ^ average Vosstian iron particle size 10 " steel plate D ^ average previous Voss back iron particle size 10 rolled steel plate D effective particle size although the present invention will be based on its better The specific embodiments of this document must be understood that the present invention is not limited to this. On the contrary, the present invention will cover all replacements, modifications and equivalent situations that can be included in the spirit and scope of the present invention. "CNS) A4 specification (210X297 public n) —I; ---------------- ir ------ V (" Read the back note first ^^ > Re-enter the item. '&Quot; This page) -9-Λ7: ^ 10 ^ V. Explanation of invention (7) Definition of additional patent application scope. " Please read the notes on the back before filling this page) Detailed description of the invention The present invention is about a novel HSLA steel that meets the above-mentioned challenges. The present invention is based on providing both the essence and the strengthening of the microstructure. A novel combination of steel chemistry and treatment that reduces D Β Τ ′ T and strengthens toughness under tensile strength. The essential strengthening is achieved through the correct judgment balance of important alloy elements in the steel, as described in detail in the description of the present invention. The structural strengthening comes from achieving very fine effective particle size and making finely grained Asada loose iron and / or low-toughness iron bars. The average size of the fine particles is much smaller than the previous Vostian iron particles. In addition, In the tempering process of the Asada loose iron / toughened iron structure of the present invention, the strength and toughness can be optimized by using the dispersion strengthened from copper precipitates and mixed carbides / carbonitrides. Staff of the Intellectual Property Bureau of the Ministry of Economic Affairs Printed by a consumer cooperative. According to the foregoing description, a method for preparing a steel plate is provided, in which the microstructure contains markedly tempered finely-granulated strips. 2. Tempering micro-granulated low-toughness iron or a mixture thereof, wherein the steps of the method include (a) substantially uniforming the steel block (1) substantially uniforming the steel block, and (ii) substantially dissolving the niobium and vanadium in the steel block. All of the carbides and carbonitrides, and (1 1 i) are reheated at the temperature at which the fine primary Vostian iron particles are established in the steel plate: (b) shrinking steel plates, recrystallized at Vostian iron In the first temperature range, steel plates are formed under one or more hot-rolling channels; (c) in the second temperature range below a temperature of about T "^ but above about the transformation temperature of A r 3, in a Or further reduce the steel plate under the hot-rolling channel; (This paper size applies the Chinese National Standard (CNS) A4 specification (210 X 297 gong)) -10- 459052 Λ7 B7 Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs Description of the invention (8) d) The steel sheet is quenched to a temperature lower than about M s at a cooling rate of about 10 t / s to about 40 t / s (18 T / s-7 2 F / s) per second. The above 200. (: quenching stop temperature of (360 ° F); (e) stop quenching; and (f) at about 4 0 0 t (7 5 2 T) to about A. The tempering temperature of the steel plate at the tempering temperature of the transformation temperature of I, preferably as high as but excluding the transformation temperature of A ^ i, is sufficient for the precipitation hardening particles, that is, one or A variety of ε-copper, Mo2C, or niobium and vanadium carbides and carbonitrides, the time sufficient to precipitate hardened particles is mainly determined by the thickness of the steel plate, the chemistry of the steel plate, and the tempering temperature, and can be cooked by this The artist decides that (see the appendix for the definition of saliency, hardened particles, Tur temperature, Ar 3, M, and A.i conversion temperature.) In order to determine the room temperature and low temperature toughness, the steel according to the present invention preferably contains mainly Tempered, micro-granulated, low-toughness iron, tempered micro-granulated Asada iron, or a mixture thereof. It is preferable to substantially reduce the formation of embrittlement components such as upper toughened iron, twin crystal Asada iron, and M A. In the scope of the description and patent application of the present invention, a significantly means that at least about 50% by volume, and the microstructure more preferably contains at least about 60% by volume to about 80% by volume of tempered micro-granulation and low toughness. Iron, tempered micro-granulated Asada loose iron or mixtures thereof, and the microstructure more preferably contains at least about 90% by volume of tempered micro-granulated low-toughened iron, tempered micro-granulated Asada loose iron or The mixture, the microstructure, most preferably contains substantially 100% tempered fine-grained strips of Asada loose iron. The steel sheet processed according to the present invention is manufactured in a known manner. In a specific embodiment, it contains iron and the following alloying elements, which is more suitable as shown in the following table. 1 This paper size applies the Chinese National Standard (CNS) A4 specification (210 x 297) Public Love> -11------------- ί ^ -------- ^ --------- line one {Please read the notes on the back before filling This page) A7 459052 _______ Η 7 V. The weight range shown in the description of the invention: Table I Range of alloy element (% by weight) Carbon (C) 0.04-0.12, more preferably 0.04-0.07 Manganese (Μη) 0.5-2.5 , More preferably 1.0-1.8 nickel (Ni) 1.0-3.0, more preferably 1.5-2.5 copper (Cu) 0.1-1.5, more preferably 0.5-1.0 molybdenum (Mo) 0.1-0.8, more preferably 0.2-0.5 niobium (Nb) 0.02-0.1, more preferably 0.03-0,05 titanium (Ti) 0.008-0.03, more preferably 0.0 0,02 aluminum (A1) 0.001 -0.05, more preferably 0.005 -0.03 nitrogen (N) 0,002 -0.005, more preferably 0.002-0.003 (Xu first read the precautions and fill in this I)

、1T 經濟部中央標準局員工消費合作社印製 有時候將釩（ν)加入鋼材中，較宜至多約〇 . 10 重量％，且更宜約0.02重量％約〇.05重量％。 有時候將鉻（Cr)加入鋼材中，較宜至多約1 . 0 重量％，且更宜約0.2重量％約0.6重量％。 有時候將矽（Si)加入鋼材中，較宜至多約0 . 5 重量％，且更宜約0.01重量％約0.5重量％，且又 更宜約0 . 0 5重量％約0 . 1重量％。 有時候將硼（B )加入鋼材中，較宜至多約 0.0020重量％，且更宜約0.0006重量％約 0 . 0 0 1 0 重量 ％。 本紙張尺度適用中國國家標準（CNS ) Λ4規格（210Χ297公筇） -12- 經濟部中央標準局負工消费合作社印製 Α7 Β7 五、發明説明彳0 ) 這些鋼材較宜含至少約1重量％鎳，鋼材之鎳含量必 要時可增加至約3重量％，以強化熔接後之性能，每增加 1重量％的鎳，預期可使鋼材之DBTT下降約l〇°C ( 1 8 T)，鎳含量較宜低於9重量％，更宜低於約6重量 %，鎳含量較宜減至最低以減低鋼材之成本，如果鎳含量 增加約3重量％，錳含量可下降至約0·5重量％至 0 . 0重量％。 此外，鋼材中的殘留物較宜實質上最少化，磷（P ) 含量較宜低於約0 . 0 1重量％，硫（S)含量較宜低於 約0 . 004重量％，氧（〇）含量較宜低於約0 . 00 2重量％。1, 1T Printed by the Consumer Cooperatives of the Central Standards Bureau of the Ministry of Economic Affairs Sometimes vanadium (ν) is added to steel, preferably at most about 0.10% by weight, and more preferably at about 0.02% by weight and about 0.05% by weight. Sometimes chromium (Cr) is added to the steel, preferably at most about 1.0% by weight, and more preferably about 0.2% by weight to about 0.6% by weight. Sometimes silicon (Si) is added to the steel, preferably up to about 0.5% by weight, more preferably about 0.01% by weight, about 0.5% by weight, and still more preferably about 0.05% by weight, and about 0.1% by weight. . In some cases, boron (B) is added to the steel, preferably at most about 0.0020% by weight, and more preferably at about 0.0006% by weight and about 0.000 10% by weight. This paper size applies the Chinese National Standard (CNS) Λ4 specification (210 × 297 gong) -12- Printed by the Consumers' Cooperative of the Central Standards Bureau of the Ministry of Economic Affairs A7 B7 V. Description of the invention 彳 0) These steels should preferably contain at least about 1% by weight The nickel content of nickel and steel can be increased to about 3% by weight if necessary to enhance the performance after welding. For every 1% by weight of nickel, the DBTT of steel is expected to decrease by about 10 ° C (18 T). The content is preferably less than 9% by weight, more preferably less than about 6% by weight. The nickel content is preferably minimized to reduce the cost of steel. If the nickel content is increased by about 3% by weight, the manganese content can be reduced to about 0.5% by weight. % To 0.0% by weight. In addition, residues in the steel are preferably substantially minimized. The content of phosphorus (P) is preferably less than about 0.01% by weight, the content of sulfur (S) is preferably less than about 0.004% by weight, and oxygen (〇) ) The content is preferably less than about 0.002% by weight.

鋼板之處理 (1 )降低 D B T T 達到低的D B T T例如低於約一 7 3 °C (— 1 0 0 T )，爲發展新的HSLA鋼材供低溫應用之主要挑戰，技 術挑戰是在目前的H S L A技術下維持/增加強度且同時 降低DBTT,尤其是在HAZ中，本發明利用合金及處 理之組合，同時改變耐破斷性之本質及微結構促成因素， 如同下文所述，製造在底板及H A Z中具有極佳低溫性質 之低和今鋼材 在本發明中，微結構韌性是利用降低鋼材的D B T 丁 ，此微結構韌性之一個主要成份是包括精煉先前的沃斯田 鐵粒子大小及改良粒子之形態，針對強化鋼板中每單位體 本紙張尺度適用中國國家標準（CNS } Λ#兄拮（210X297公# ) (誚先閱讀背面之注意事項再填寫本頁) •1Τ -13- 經濟部中央標準局貝工消費合作社印聚 A7 B7_____ 五、發明説明“) 積高角晶界之界面，類似於熟諳此藝者所熟悉的，此處所 稱的"粒子"係指多晶物質中的個別晶體，且此處所稱的 "粒子界面"係指相對於從一個結晶向轉化成另一個結晶 向時，在金屬內的狹窄區域，此處所稱的 '"高角晶界〃係 指分隔兩個結晶向差異大於約8 °之相鄰粒子的粒子界面， 同時此處所稱的""高角晶界"係指有效作爲高角晶界之界 面，也就是說可偏斜裂縫或破斷傳導且因此扭曲破斷路徑 之界面。 從熱機械控制的輥軋處理（TMC P )至每單位體積 高角晶界總界面面積之促成因素s v，可用下列公式定義： & = 士〔1 十 i? + *) + 0.63(r - 30) 其中： d爲熱輥軋鋼板在其中沃斯田鐡不會結晶之溫度範圍 內輥軋前之沃斯田鐵平均粒子大小（先前沃斯田鐵粒子大 小）； R爲減縮率（原始鋼板厚度/最終鋼板厚度）；且 r爲由於在其中沃斯田鐵不會結晶之溫度範圍內熱車昆 軋之鋼材厚度減縮％。 熟知於此項技藝，當鋼材之Sv增加時，由於在高角晶 界破斷路徑之裂縫偏斜及破斷扭曲而使DBTT下降，# 商業化TMCP實務中，特定鋼材厚度之R値囿定且1_値 之上限通常爲7 5，固定R及r値，從上列公式很明顯地 本紙張尺度適用中國國家標準（CNS ) A4規格（2iOX297^^ "' -14 - 誚先閱讀背面之注意事項再填寫本1) *1Τ A7 Η 7 經濟部中央標準局貝工消費合作社印製 五 、發明説明<!2 ) 1 1 了 解 S V只能經由降低d而實質上增加， 根據本發弓 月爲了降 1 1 低 鋼 材 中的d 値，結合使 用 T i — Ν b 微 合 金 化 及 最佳化 1 1 的 T Μ C P實 務，對於熱 輥 軋 / 變 形 過 程 之 相 同 總 減縮量 ik ά I 1 具 有 最初較 細沃斯 田鐵 平 均粒 子 大小 之 鋼 材 將 導 致較細 閱 讀 1 的 完成化沃斯 田鐵平均粒 子 大小 > 因 此在本 發 明 中 ，將 ?! -ί \ I T i — N b之 添加量 最適 化 J 以 便在 T Μ C Ρ 過 程 中減少 注 $ 事 1 1 再 度 加 熱同時 產生所 需的 沃 斯 田 鐵 粒 子 成 長 抑 制 性 ，參照 項 填 1 丄 圖 1 A ，使用 相當低 的再 度 加 熱 溫 度 > 較 宜 約 9 5 5 °C至 % 本 页 [ 約 1 0 6 5 °C (17 5 0 T ~ 1 9 5 0 Τ ) > 在 再 度加熱 1 I 鋼 板 塊 1 0 ^ 於熱變 彤前 得 到 之 最 初沃斯 田 鐵 平均粒子大 1 1 I 小 D - 低於約 12 0 微米 > 根 據 本 發 明 之 處 理 可 防 止傳統 1 1 的 T Μ c P由 於使用 ** Ira" 較闻 的 加 熱 溫 度 例 如 高 於約 1 0 9 5 訂 1 V ( 2 0 0 0 〇F )而 造成 之 沃 斯 田 鐵 ife丄 杻 子 過 度 成 長 。爲了 1 | 促 進 動 態再結 晶引起 的粒 子 梢 煉 在其 中 沃 斯 田 鐵 再結晶 1 I 溫 度 範 圍內之 熱輥軋 過程 中 J 使 用 每 次 通 過 之 重 EB. 里 減低大 1 1 於約 1 0 %。 現在參 照圖 1 B ί 根 據 本 發 明 之 處 理 ，鋼板 1 塊 1 0 〃在其 中沃斯 田鐵 再 結 晶 之 溫 度 範 圍 內 熱 輥 軋（變 I I 形 ) 後 但在其 中沃斯 田鐵 不 會 再 結 晶 之 溫 度 範 圍 內 熱輥軋 i I 刖 > 平均先前 沃斯田 鐵粒 子 大小 D ff ( 也 就 是 d ) 低於約 1 1 I 3 0 微 米，較 宜低於 2 0 微 米 > 且 更 宜 低於約 1 0 微米。 1 1 此外 J 爲了在 整個厚 度方 向 產 生有效的粒子 大小 減 縮，在 1 [ 低於約 T 福 1度但高於約A r 3 轉 化 之 溫 度 範 圍 內 進行重 1 | 量 減 縮 ，較宜 累積超 過約 7 0 % 〇 現 參 照 ΪΞΓ 圖 1 C ，根據 1 1 本 發 明 之T Μ C P在 整個 厚 度 方 向 具 有非常 細 的 有效粒子 1 i 1 本紙張尺度適用中國囤家標準（CNS ) Λ4规梢（2!0X29"7公荩） -15- 經濟部中央標準局員工消費合作社印聚 Λ7 Η 7 五、發明説明ί3 ) 大小D 之完成輥軋後的鋼扳1 0 上導致形成伸長化塊 狀粒子結構，例如有效粒子大小D 低於約1 〇微米，較 宜低於約8微米> 且更宜低於約5微米，熟諳此藝者將可 了解，如此可強化鋼板1 0 "每單位體積高角晶界之界面 面積，例如1 1。 在稍微更詳細的說明中，製備根據本發明之鋼材是經 由形成如同上述所需組成之鋼板塊；將鋼板塊加熱至約 9 5 5 °C 至約 1 0 6 5 °C ( 1 7 5 0 °F - 1 9 5 Ο Τ )之The processing of steel plates (1) reduces the DBTT to a low DBTT, for example, below about 73 ° C (—100 T). This is the main challenge for the development of new HSLA steels for low temperature applications. The technical challenge is in the current HSLA technology. To maintain / increase strength while reducing DBTT, especially in HAZ, the present invention utilizes a combination of alloys and treatments, while changing the nature of breakage resistance and microstructural enablers, as described below, manufactured in baseplates and HAZs Low-temperature steel with excellent low-temperature properties. In the present invention, the microstructural toughness is to reduce the DBT of steel. One of the main components of this microstructural toughness is to refine the size of the previous Vostian iron particles and improve the shape of the particles. For the paper size per unit body in the reinforced steel sheet, the Chinese national standard (CNS} Λ # 兄 拮 (210X297 公 #) applies (诮 Please read the precautions on the back before filling this page) • 1Τ -13- Central Bureau of Standards, Ministry of Economic Affairs Bei Gong Consumer Cooperative Co., Ltd. A7 B7_____ 5. Description of the invention ") The interface of the high-angle grain boundary is similar to the one familiar to this artist. The" particle "here is called Refers to individual crystals in a polycrystalline substance, and the "particle interface" referred to herein refers to a narrow region within a metal as it is converted from one crystal to another crystal direction. High-angle grain boundary 〃 refers to the particle interface separating two adjacent particles whose crystal orientations differ by more than about 8 °. At the same time, " " High-angle grain boundary " refers to the interface that is effective as a high-angle grain boundary, that is, The interface that can deflect cracks or fracture conduction and thus distort the fracture path. From the thermomechanically controlled rolling treatment (TMC P) to the total interface area per unit volume of the high-angle grain boundary, the contributing factor sv can be defined by the following formula: & = taxi [1 ten i? + *) + 0.63 (r-30) where: d is the average particle size of Vosstian iron before rolling in the temperature range where Vossfield wo n’t crystallize Size (previously Vosstian iron particle size); R is the shrinkage reduction ratio (original steel plate thickness / final steel plate thickness); and r is the reduction in thickness of the hot-rolled rolled steel due to the temperature range in which Vosstian iron does not crystallize . Familiar with this As the Sv of steel increases, DBTT decreases due to the deflection of cracks and fracture distortion in the fracture path of high-angle grain boundaries. #Commercialized TMCP practice, the R of a specific steel thickness is fixed and 1_ 値 of The upper limit is usually 7 5. Fixed R and r 値. From the above formula, it is clear that the paper size applies the Chinese National Standard (CNS) A4 specification (2iOX297 ^^ " '-14-诮 Read the precautions on the back before filling (1) * 1T A7 Η 7 Printed by the Shellfish Consumer Cooperative of the Central Standards Bureau of the Ministry of Economic Affairs 5. Description of the invention <! 2) 1 1 Understand that SV can only be substantially increased by decreasing d, according to the present month in order to reduce 1 1 D 中 in low steel, combined with T i — Ν b micro-alloying and optimization T 1 CP practice of 1 1 for the same total reduction in the hot rolling / deformation process ik ά I 1 has an initially finer Steel with an average particle size of Staples iron will result in a more detailed reading of the average particle size of Vosted iron > Therefore, in the present invention, the addition amount of?! -Ί \ IT i — N b is optimized J In order to reduce the amount of injection during T Μ C Ρ event 1 1 re-heating while producing the required growth inhibition properties of Vostian iron particles, fill in the reference 1 1 Figure 1 A, it is better to use a relatively low re-heating temperature > Approx. 9 5 5 ° C to% This page [Approx. 1 0 6 5 ° C (17 5 0 T ~ 1 95 0 Τ) > Reheat 1 I steel block 1 0 ^ The average particle size of Vosstian iron is 1 1 I small D-less than about 120 micrometers. The treatment according to the present invention can prevent the conventional T Μ c P of 1 1 due to the use of ** Ira " higher heating temperature such as higher than About 1 0 9 5 Order 1 V (2 0 0 〇F) caused the excessive growth of Vostian iron ife. For 1 | Promote dynamic recrystallization of particle smelting caused by hot rerolling of Vosstian iron in the temperature range of I I during the hot rolling process J Use the weight of each pass EB. Reduce by 1 1 to about 10% . Referring now to FIG. 1B, according to the processing of the present invention, a steel plate 1 10 〃 is hot rolled (transformed into a shape II) within a temperature range in which Vosstian iron is recrystallized but in which Vosstian iron does not recrystallize. Hot rolling i I 刖 > average previous Vosstian iron particle size D ff (ie d) below about 1 1 I 3 0 microns, more preferably below 20 microns > and more preferably below about 10 micron. 1 1 In addition, J In order to produce effective particle size reduction in the entire thickness direction, the weight reduction is performed within the temperature range of 1 [below about T and 1 degree but above about A 3 conversion, and it is better to accumulate more than about 70% 〇 Referring now to Figure 1C, according to 1 1 the T Μ CP of the present invention has very fine effective particles in the entire thickness direction 1 i 1 This paper size is applicable to the Chinese standard for storage (CNS) Λ4 gauge (2! 0X29 " 7mm 荩) -15-Industrial Consumer Cooperative of the Central Standards Bureau of the Ministry of Economic Affairs, Yinju Λ7 Η 7 V. Description of the invention ί 3) After the rolling of the steel plate 10 of size D, an elongated massive particle structure is formed, For example, the effective particle size D is less than about 10 microns, more preferably less than about 8 microns > and more preferably less than about 5 microns. Those skilled in the art will understand that this can strengthen the steel sheet 10 " high angle per unit volume The interface area of the grain boundary, such as 1 1. In a slightly more detailed description, the steel according to the present invention is prepared by forming a steel block having the desired composition as described above; the steel block is heated to about 9 5 5 ° C to about 1 0 6 5 ° C (1 7 5 0 ° F-1 9 5 Ο)

溫度：在其中沃斯田鐵再結晶之第一個溫度範圍也就是高 於約Tnr溫度下，一或多道次熱輥軋鋼板塊而形成鋼板， 提供約3 0%至約7 0%的減縮，在低於約Τη，溫度但高 於約A r 3轉化溫度之第二個溫度範圍下，進一步一或多道 次熱輥軋鋼板，提供約40%至約80%的減縮，然後使 熱輥軋後的鋼板在每秒約1 0 °C至每秒約4 0 °C ( 1 8 T /秒一 7 2 °F /秒）之冷卻速率下淬火至適當的Q S T低 於約M s轉化溫度加上2 0 0 °C ( 3 6 0 °F )，此時終止淬 火，在本發明之一個具體實施例中，使鋼板空氣冷卻至環 境溫度，使用此處理製造的微結構較宜主要含微細粒化條 麻田散鐵、較少量的微細粒化變韌鐵、或其混合物，或更 宜實質上含1 0 0%的微細粒化條麻田散鐵。 根據本發明如此直接淬火之麻田散鐵鋼材具有高強度 且其韌性可經由在約4 0 0 °C ( 7 5 2 °F )至約A。i轉化 溫度的適當溫度範圍下回火而改進，在此溫度範圍下回火 鋼材也導致淬火應力之減低且因而導致強化軔性，雖然回 本紙張尺度適用中國國家標準（<：1^)八4規栝（2!0/297公耷） ί"先間讀背面之注意事項乔填寫本頁) 衣· 、1Τ -16- Λ7 B7 459052 五、發明說明（14 ) 火可強化鋼材之韌性，其通常導致強度的實質上損失，在 本發明中，回火之一般強度損失可經由使沈澱物分散硬化 而抵銷，利用細銅沈澱物及混合的碳化物及/或碳氮化物 之分散硬化，使麻田散鐵結構在回火時的強度及韌性最適 化，本發明鋼材的獨特化學性，使其可在約4 0 0 °C至約 650 t (750 °F -120 0 °F)的大範圍內回火而不 會明顯地損失淬或強度，此鋼板較宜在約4 0 0 °C ( 7 5 2 °F )至低於A t 1轉化溫度之回火溫度下回火一段足 夠的時間，使硬化的粒子（如本文之定義）沈澱，此方法 可促進鋼板微結構之轉化，使其主要爲回火的微細粒化條 麻田散鐵、回火化微細粒化低變韌鐵、或其混合物，再一 次，足以造成硬化粒子沈澱之時間主要決定於鋼板之厚度 、鋼板之化學性、及回火溫度，且可由熟諳此藝者決定。 熟諳此藝者將可了解，本文所稱的厚度減縮％係指後 鋼板或鋼板在所稱減縮前的厚度減縮％，僅供說明之目的 而不作爲本發明之限制，約2 5 . 4公分（1 0吋）厚度 之鋼板塊可在第一個溫度範圍減縮約5 0% ( 5 0減縮％ )至厚度爲約1 2 · 7公分（5吋），然後在第二個溫度 範圔減縮約8 0 % ( 8 0減縮％ )至厚度爲約2 . 5公分 (1吋），在此所稱的w鋼板塊#係指任何大小之鋼材。 鋼板塊較宜經由適當的方式加熱，將實質上整個鋼板 塊且較宜爲整個鋼板塊之溫度提昇至所需的再度加熱溫度 ，例如將鋼板塊放在爐中一段時間，在本發明範圍內任何 本紙張尺度適用中國國家標準（CNS)A4規格（2!0 X 297公釐） -- - - - - ------~装·-----II 訂 — — — — — —丨 II ~ (請先閱讀背面之;i意事項再填寫本頁) 經濟部智慧財產局員工消費合作社印製 -17- 經濟部中央標隼局員工消費合作社印裝 A7 137 五、發明説明ij5 ) 鋼材組成物必須使用之特定再度加熱溫度，熟諳此藝者可 輕易地從實驗或使用適當的模式計算而決定，此外，將實 質上整個鋼板塊且較宜爲整個鋼板塊的溫度提昇至所需的 再度加熱溫度所需的爐溫及再度加熱時間，熟諳此藝者可 參考標準的工業應用而輕易地決定。 除了施加至實質上整個鋼板塊之再度加熱溫度以外， 描述本發明處理方法提到的另一溫度爲在鋼材表面測量之 溫度，鋼材之表面溫度可用例如光學高溫計或其他適於測 量鋼材表面溫度之任何器材測量，在本文提到的冷卻速率 爲在鋼板厚度中心或實質上中心之冷卻速率；且淬火停止 溫度（Q S T )爲停止淬火後，由於熱從鋼板厚度中心傳 送而使鋼板表面達到的最高或實質上最高之溫度，例如處 理根據本發明鋼材組成物之實驗熱時，將熱電偶放在鋼板 厚度之中心或實質上的中心供測量溫度，並使用光學高溫 計測量表面溫度，發展中心溫度與表面溫度之相關性供後 續處理相同或實質上相同的鋼材組成物使用，如此可經由 直接測量表面溫度而決定中心溫度，同樣地，熟諳此藝者 可參考標準工業應用，決定完成所要的加速冷卻速率所需 的溫度及淬火液體之流速。 對於本發明範圍內之任何鋼材組成物，定義再結晶範 園與非再結晶範圍界面之溫度，Tnr溫度，決定於鋼材之 化學性且尤其是碳濃度及鈮濃度、輥軋前的再度加熱溫度 、及輥軋道次中所給定之減縮量，熟諳此藝者可根據本發 明，經由實驗或模式計算，決定特殊鋼材之此溫度。同樣 本紙張尺度適用中國國家標準（CNS )厶4規梢（210X297公 誚先閱讀背而之注意事項再填艿本頁) 衣 訂 -18- Λ7 Η 7 五、發明説明k ) 地，熟諳此藝者可根據本發明，經由實驗或模式計算本文 中提到的A。i、A r 3、M s轉化溫度。 雖然上述的微結構方式可用於降低基質鋼板之 DBTT，其在熔接HAZ的粗粒化區域無法完全有效地 維持足夠低的DBTT,因此，利用下述之合金元素本質 效應，本發明提供在熔接HAZ的粗粒化區域維持足夠低 的DBTT之方法。 經濟部中央標準局負工消費合作社印製 (請先閲讀背而之注意事項再填寫本頁) 目前肥力鐵低溫鋼材通常是以體心立方（B C C )晶 格爲基質，雖然這種結晶系統可以在低成本下提供高強度 ，當溫度降低時，其有從延性驟變轉化成破斷性之問題， 此可基本上歸因於B C C系統的臨界變形剪應力（ CRSS)(本文定義）對溫度之強烈敏感性，其中 CRSS隨著溫度下降而快速上升，造成剪力進行且導致 延性破斷更困難，反之，脆裂破斷進行例如分解對於溫度 較不敏感，因此，當溫度降低時，分解變成有利的破斷模 式，導致引發低能脆裂破斷，C R S S爲鋼材之本質性質 ，且敏感於變形時可橫越滑移之差排的容易性，也就是說 橫越滑移較容易之鋼材將有低的C R S S及因此有低的 DBTT.，部份面心立方（FCC)安定劑例如N i已知 可促進橫越滑移，而BCC安定合金元素例如S i、A 1 、：Mo、Nb及V可降低橫越滑移，在本發明中，FCC 安定合金元素例如N i及Cu之含量較宜最適化，考量成 本及降低DBTT之有利效益，Ni合金較宜至少約 1 . 0重量％且更宜至少約1 . 5重量％;且3<：(：安定 本紙張又度適用中國國家標隼（CNS ) A4規梠（21〇Χ2π公势) -19 - 經濟部中央標挲局貝4消費合作社印製 Λ7 B7 -^Μ·_··Μ_Ι»_I ·ι ~ - - — 一一 I * 1-.-. -·— 11 五、發明説明（^ ) 合金元素在鋼材中的含量爲實質地最少化。 由於根據本發明鋼材之化學性與處理之獨特組合導致 的本質及微結構韌化之結果，此鋼材在底板及熔接後的 HAΖ都有極佳的低溫韌性，在這些鋼材底板及熔接後的 HAZ之DBTT都低於約一 7 3〇C (― 1 0 0°F)且可 低於約-1 0 7 °C ( — 1 6 ◦ °F )。 (2)張力強度大於830Mpa (120ksi)且微 結構整個厚度之均勻性與性質 一般而言，在回火時，普通碳及沒有強烈碳化物形成 體之低合金麻田散鐵鋼材軟化或損失其淬火強度，此強度 損失之程度爲鋼材之特定化學性、回火溫度與時間之函數 ，在本發明之鋼材中，回火時損失的強度可經由硬化粒子 之微細沈澱而實質地改善，本發明鋼材之獨特化學性使得 回火可在約400 X：至約650 °C (750 T— 1200 °F)之大範圍內進行，而不會明顯地損失淬火強度，在此 大的回火範圍內，在不同溫度發生或最高化之硬化粒子沈 澱導致強化，也就是在此大範圍下，發生足量的硬化粒子 沈澱，提供累積的強度以補償通常伴隨著回火之強度損失 ，可在此大範圍內回火之處理彈性很有利。 在本發明中，所需的強度是在相當較少含量下得到， 伴隨的優點是在鋼材底板及H A Z都有可熔接性及極佳的 韌性，整個合金中較宜至少含約0 . 0 4重量％的（：，使 得到的張力強度大於830Mpa (120ksi)。 本紙張尺度適用中國國家標準（CNS > Λ4規核（210X2W公势） (請先閲讀背面之注意事項#填寫本育)Temperature: In the first temperature range where Vostian iron is recrystallized, that is, above the Tnr temperature, one or more hot rolling of the steel block to form a steel plate, providing a reduction of about 30% to about 70% In the second temperature range below about Tη, temperature but above about A r 3 transformation temperature, further one or more passes of hot-rolled steel sheet are provided to provide a reduction of about 40% to about 80%, and then the heat is reduced. The rolled steel sheet is quenched at a cooling rate of about 10 ° C per second to about 40 ° C per second (18 T / second to 72 ° F / second) to a suitable QST conversion below about M s. The temperature is increased by 200 ° C (360 ° F), and the quenching is terminated at this time. In a specific embodiment of the present invention, the steel plate is air-cooled to the ambient temperature. The finely-granulated Asa loose iron, a relatively small amount of fine-granulated and toughened iron, or a mixture thereof, or more preferably, contains 100% of the finely-granulated Asa loose iron. The Asada scattered iron steel thus directly quenched according to the present invention has high strength and its toughness can pass between about 400 ° C (75 2 ° F) to about A. i The transformation temperature is improved in the appropriate temperature range. Tempering the steel in this temperature range also results in a reduction of the quenching stress and thus the strengthening of the ductility. Although the paper size of the paper applies the Chinese national standard (<: 1 ^) Regulations of 8 (2! 0/297) ί " Precautions on the back of the first reading Joe fill in this page) Clothing, 1T -16- Λ7 B7 459052 5. Description of the invention (14) Fire can strengthen the toughness of steel It usually results in a substantial loss of strength. In the present invention, the general strength loss of tempering can be offset by dispersing and hardening the precipitate, using the dispersion of fine copper precipitates and mixed carbides and / or carbonitrides. Hardening, optimizing the strength and toughness of Asada's loose iron structure during tempering. The unique chemistry of the steel of the present invention allows it to be used at temperatures from about 40 ° C to about 650 t (750 ° F -120 0 ° F). Tempering in a wide range without significant loss of quenching or strength, this steel sheet is preferably tempered at a tempering temperature of about 4 0 ° C (7 5 2 ° F) to below the transformation temperature of A t 1 Sufficient time to precipitate hardened particles (as defined herein), this method can Promote the transformation of steel sheet microstructure, making it mainly tempered micro-granulated strip Asada loose iron, tempered micro-granulated low-toughness iron, or mixtures thereof, once again, the time sufficient to cause precipitation of hardened particles is mainly determined by the steel sheet The thickness, the chemical properties of the steel plate, and the tempering temperature can be determined by those skilled in the art. Those skilled in the art will understand that the “% reduction in thickness” referred to herein refers to the% reduction in thickness of the rear steel plate or steel plate before the stated reduction. It is for illustrative purposes only and is not a limitation of the present invention, about 25.4 cm. (10 inches) thickness of steel plate can be reduced by about 50% (50% reduction) in the first temperature range to a thickness of about 1 2 · 7 cm (5 inches), and then reduced in the second temperature range From about 80% (80% reduction) to a thickness of about 2.5 cm (1 inch), the “steel block #” referred to herein refers to any size steel. It is better to heat the steel plate block in an appropriate manner to increase the temperature of the entire steel plate block, and preferably the entire steel plate block, to the required reheating temperature. For example, placing the steel plate block in a furnace for a period of time is within the scope of the present invention. Any paper size is applicable to Chinese National Standard (CNS) A4 (2! 0 X 297 mm)----------- ~ installed · ----- II Order — — — — — —丨 II ~ (Please read the back of the page first; please fill in this page before filling in this page) Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs-17- Printed by the Consumer Cooperative of the Central Standardization Bureau of the Ministry of Economic Affairs A7 137 V. Invention Description ij5 The specific reheating temperature that the steel composition must use. Those skilled in the art can easily determine it from experiments or calculations using appropriate models. In addition, the temperature of substantially the entire steel block, and preferably the entire steel block, is increased to the required level. The furnace temperature and reheating time required for the reheating temperature can be easily determined by those skilled in the art with reference to standard industrial applications. In addition to the reheating temperature applied to substantially the entire steel block, another temperature mentioned in the description of the processing method of the present invention is the temperature measured on the surface of the steel. The surface temperature of the steel can be, for example, an optical pyrometer or other suitable for measuring the surface temperature of the steel. For any equipment measurement, the cooling rate mentioned in this article is the cooling rate at the center or substantially the center of the thickness of the steel plate; and the quenching stop temperature (QST) is the temperature reached by the surface of the steel plate due to the heat transfer from the center of the steel plate thickness after the quenching is stopped. The highest or substantially highest temperature, for example, when processing the experimental heat of the steel composition according to the present invention, the thermocouple is placed at the center or substantially the center of the thickness of the steel plate to measure the temperature, and the surface temperature is measured using an optical pyrometer to develop the center The correlation between the temperature and the surface temperature is used for subsequent processing of the same or substantially the same steel composition. In this way, the central temperature can be determined by directly measuring the surface temperature. Similarly, skilled artisans can refer to standard industrial applications and decide to complete the required Temperature and quenching fluid required to accelerate cooling rate The flow rate. For any steel composition within the scope of the present invention, the temperature at the interface between the recrystallization range and the non-recrystallization range, Tnr temperature, is determined by the chemical properties of the steel, especially the carbon concentration and niobium concentration, and the reheating temperature before rolling , And the reduction amount given in the rolling pass, a person skilled in the art can determine the temperature of the special steel according to the present invention through experiments or model calculations. Similarly, this paper size applies the Chinese National Standard (CNS) 厶 4 gauge (210X297). Please read the precautions before filling in this page.) Bookbinding-18- Λ7 Η 7 V. Description of the invention. Artists can calculate A mentioned herein through experiments or models according to the present invention. i, A r 3, M s conversion temperature. Although the above microstructure method can be used to reduce the DBTT of the matrix steel plate, it cannot fully and effectively maintain a sufficiently low DBTT in the coarse grained area of the welded HAZ. Therefore, the present invention provides a The coarse grained area of the method maintains a sufficiently low DBTT. Printed by the Central Standards Bureau of the Ministry of Economic Affairs and Consumer Cooperatives (please read the precautions before filling this page) At present, low-temperature ferrous iron steel is usually based on the body centered cubic (BCC) lattice, although this crystallization system can Provides high strength at low cost. When the temperature decreases, it has the problem of changing from ductility to breaking. This can basically be attributed to the critical deformation shear stress (CRSS) of the BCC system (defined in this article) versus temperature. Strong sensitivity, in which CRSS rises rapidly with decreasing temperature, causing shear to proceed and causing ductile fracture to be more difficult. Conversely, brittle fracture breaking such as decomposition is less sensitive to temperature. Therefore, when the temperature decreases, the decomposition becomes Favorable breaking mode leads to low-energy brittle fracture. CRSS is the essential nature of steel, and it is sensitive to the ease of cross-sliding when deforming, which means that steels that are easier to cross-slip will have Low CRSS and therefore low DBTT. Some face-centered cubic (FCC) stabilizers such as Ni are known to promote transverse slip, while BCC stabilizer alloy elements such as Si, A1 : Mo, Nb, and V can reduce the cross slip. In the present invention, the content of FCC stable alloying elements such as Ni and Cu should be optimized. Considering the cost and the beneficial effect of reducing DBTT, the Ni alloy is preferably at least about 1 0% by weight and more preferably at least about 1.5% by weight; and 3 <: (: Stable this paper is again applicable to China National Standard (CNS) A4 Regulations (21〇 × 2π public power) -19-Central Ministry of Economic Affairs Printed by the Standards Bureau 4 Consumer Cooperative Λ7 B7-^ Μ · _ ·· Μ_Ι »_I · ι ~---One by one I * 1 -.-.-· — 11 V. Description of the invention (^) The content of the steel is substantially minimized. As a result of the inherent and microstructural toughening caused by the unique combination of the chemical properties and processing of the steel according to the present invention, the steel has excellent low temperature toughness on the base plate and after welding. The DBTT of these steel base plates and HAZ after welding are lower than about 730 ° C (―100 ° F) and can be lower than about -10 ° C (--16 ° F). 2) Tensile strength is greater than 830Mpa (120ksi) and the uniformity and properties of the entire thickness of the microstructure Generally speaking, when tempering, ordinary carbon and no strong carbonization The low-alloyed Masada loose iron steel of the material forming body softens or loses its quenching strength. The degree of strength loss is a function of the specific chemical properties of the steel, the tempering temperature and time. In the steel of the present invention, the strength lost during tempering It can be substantially improved through the fine precipitation of hardened particles. The unique chemistry of the steel of the present invention allows tempering to be performed within a wide range of about 400 X: to about 650 ° C (750 T- 1200 ° F) without The quenching strength is obviously lost. Within this large tempering range, precipitation of hardened particles that occurs or maximizes at different temperatures leads to strengthening, that is, under this large range, sufficient precipitation of hardened particles occurs, providing cumulative strength to Compensation usually accompanies the loss of tempering strength, and the flexibility of tempering that can be tempered over this wide range is very advantageous. In the present invention, the required strength is obtained at a relatively small amount, with the accompanying advantages that both the steel base plate and the HAZ have weldability and excellent toughness, and it is preferable that the entire alloy contains at least about 0.4 (By weight, the tensile strength obtained is greater than 830Mpa (120ksi). This paper size applies to Chinese national standards (CNS > Λ4 Regulation (210X2W)) (Please read the precautions on the back first # Fill this education)

*1T 20- 459052 ；； _ 五、發明説明“） 在根據本發明之鋼材中，在考量鋼材最大可得到的強 度下，雖然除了c以外之合金元素實質上並不重要，需要 這些元素以提供所需的微結構整個厚度之均勻性及厚度大 於約2 . 5公分（1吋）之鋼板強度及供處理彈性所需的 冷卻速率範圍，此點很重要，因爲在厚鋼板中間部份之實 際冷卻速率低於表面，表面及中間的微結構可因此相當不 同，除非消除鋼材對於鋼板表面與中間部份之冷卻速率差 異之敏性，在此考量下，Μη及Mo合金添加物，且尤其 是Mo與B之組合添加物特別有效，在本發明中，考慮可 硬化性、可熔接性、低DBTT及成本而將這些添加物最 適化，如同本專利說明先前所述，從降低D B T T之觀點 ，必須使總B C C合金添加物保持最小量，設定較佳的化 學標的及範圍以達到本發明的這些及其他要求。 (3 )低熱輸入熔接之優越的可熔接性 經濟部中央標嗥局員工消費合作社印製 (誚先閱讀背而之注^^項再填寫本頁) 本發明之鋼材是設計成具有優越的可熔接性，最重要 的考量，尤其是低熱輸入熔接，爲粗粒化HAZ之冷裂化 或氫裂化，頃經發現本發明之鋼材，冷裂化敏性決定性地 受到碳含量及HAZ微結構形式而影響，而不是先前技藝 中視爲決定性參數之硬度及碳相當物，當鋼材在沒有或低 預熱（低於約1 0 0 t ( 2 1 2 T ))熔接情形下熔接時 ，爲了避免冷裂化，較佳的碳添加量上限爲約0.1重量 %，在本文中使用且不已任何方式限制本發明，"低熱輸 入熔接"係指電弧能量至多約2 5千焦耳每毫米（千焦 本纸張尺度適用中國國家橾準（CNS ) A4%拮（210x297公# > -21 - 經濟部中央標準局員工消費合作社印取 Α7 __ H7 五、發明説明彳9 ) 耳/毫米）（7. 6千焦耳/吋）之熔接。 較少的變韌鐵或自動回火條麻田散鐵微結構提供優越 的抗冷裂化性，本發明鋼材中的其他合金元素經小心地平 衡、相稱於可硬化性及強度的需求，確使在粗粒化HAZ 形成這些所要的微結構。 合金元素在鋼板塊中的角色 本發明各種合金元素的角色及較佳的濃度限制說明如 下： 碳（C )爲鋼材中其中一種最有效的強化元素，其也 可與鋼材中的強碳化物形成物例如T i、N b、V及Μ 〇 結合而在回火時提供粒子成長抑制性及沈澱強化，碳也可 促進可硬化性，也就是說冷卻時在鋼材中形成更硬更強的 微結構，如果碳含量低於約0.04重量％，不足以在鋼 材中引發所需的強化，即大於830Mpa (120 k s i )之張力強度，如果碳含量大於約0 . 1 2重量％ ，鋼材在熔接時容易冷裂化，且鋼板及其HAZ在熔接時 之韌性減低，碳含量較宜爲約0 ·◦ 4重量％至約 0 · 1 2重量％，以產生所需的強度及HAZ微結構，即 自動回火化條麻田散鐵及較少量的變韌鐵，碳含量的上限 更宜爲約0.07重量％。 錳（Μ η )爲鋼材中的基質強化劑且也可強烈地促進 硬化，爲了在厚度大於約2.5公分（1吋）的鋼板得到 所要的強度，最少量較宜爲0 _ 5重量％ Μ η ,且至少約 本紙張尺度適用中國國家標芈（CNS ) Λ4«1相U10X297公势） mV t^in n ^^^^1 ^^^^1 ^^^^1 ^^—^1 ^^^^1 (請先閱讀背面之注意事項#填，?ξ本i ) -22- A7 _____H7 五、發明説明) 1 . 0重量％Mn之最少量更佳，但是太多的Μη有害於 韌性，所以本發明較佳的上限爲約2 . 5重量％ Μ η，此 上限也較宜實質地最小化中央線偏析，其容易發生在高 Μ η及連續鑄造該材及伴隨的微結構中整個厚度非均勻性 及性質，Μ η含量之上限更宜爲約1 . 8重量％，如果鎳 含量上增約3重量％，可以不需添加錳而達到所需的高強 度，因此，廣義地說，至多約2 . 5重量％猛較宜。 矽（S i )可添加至鋼材中供去氧化之目的，且此目 的之最小量爲約0 . 0 1重量％，但是S i爲強烈的 B C C安定劑且因此增加D B TT及對韌性有負面效應， 基於這些理由，當加入S i時，上限較宜爲約〇 . 5重量 %S i，當加入S i時，S i含量之上限更宜爲約〇 . 1 重量％，去氧化並非一定需要矽，因爲鋁或鈦也可進行相 同的功能。 經濟部中央標準局男工消費合作社印製 (請先閱讀背而之注意事項再填寫本頁) 鈮（N b )的加入是促進鋼板輥軋後微結構的粒子精 煉，其可同時改進強度及韌性，熱輥軋時的鈮碳化物及碳 氮化物沈澱可阻止再結晶化及抑制粒子成長，因此提供沃 斯田鐵粒子精煉，而且回火時的鈮碳化物及碳氮化物沈澱 可提供所需的二次硬化，以補償在高於約5 0 0 °C ( 9 3 0°F)時回火通常觀察到的強度損失，基於這些理由 ，至少約0 . 02重量％Nb較宜，且至少約〇 . 03重 量％Nb更宜，但是Nb爲強的BCC安定劑且因此可增 加DBTT,太多的Nb有害於可熔接性及HAZ韌性， 所以最大量約〇 · 1重量％較佳，Nb含量之上限更宜爲 本紙張尺度適用中國國家標準（CNS ) Λ4規格（210x297公i ) -23- 經濟部中央標準局員工消費合作社印裝 A7 137 五、發明説明h ) 約0 . 0 5重量％。 釩（V )有時候加入以得到沈澱強化，回火時在鋼材 及熔接後冷卻時在HA Z中形成釩的碳化物及碳氮化物細 小粒子，當溶解在沃斯田鐵時，V對可硬化性有強烈的效 益，當V添加至本發明之鋼材後，至少約〇·02重量％ V較佳，但是過量的V將促成熔接時的冷裂化，且有害於 基質鋼材及其HAZ之韌性，因此V之添加較宜限定在最 多約0.1重量％，且更宜限定在最多約0.05重量％ 〇 鈦（T i )，當加入少量時，可有效形成氮化鈦（ T i N)粒子，其在鋼材的輥軋後結構及HAZ都可精煉 粒子大小，因此，可改進鋼材之韌性，τ i之添加量是使 Ti/N之重量比例較宜爲約3·4, Ti爲強的BCC 安定劑且因此可增加DBTT,太多的Ti經由形成較粗 的T i N或碳化鈦（T i C )粒子而不利於韌性，T i含 量低於約0.008重量％通常無法提供足夠細的粒子大 小或連結鋼材中的N而形成T i N，且大於約〇 . 〇 3重 量％可造成韌性惡化，鋼材更宜含至少約0.01重量％ Τί且不超過約0.02重量％丁1。 鋁（A 1 )添加至本發明鋼材中是供去氧化之目的， 至少約0.001重量1較宜供此目的，且更宜至少 約0 . 00 5重量％A 1，A 1也可連結溶解在HAZ中 的氮，但是A 1爲強烈的B C C安定劑且因此增加 DBTT,如果A 1含量太高，也就是高於約0 /0 5重 本紙張尺度適用中國國家標準{ CNS ) Λ4规格（210X 297公势） - ^^^1 In m I m-^. (誚先閱讀背面之注意事項再填寫本頁) -24- Λ7 _ Η 7 五、發明説明如） 量％，傾向於形成氧化鋁（A 1 2 0 3 )型摻混物，其容易 有害於鋼材及HAZ之韌性，A 1含量之上限更宜爲約 〇 · 0 3重量％。 鉬（Μ 〇 )在直接淬火時可增加鋼材之可硬化度，尤 其是與硼及鈮之組合，Μ 〇也可經由提供細小的Μ 〇 2 C碳 化物，在鋼材回火時可促進二次硬化，較宜至少約0 . 1 重量％Μο,且至少約0 . 2重量％Μο更佳，但是，* 1T 20-459052 ;; _ V. Description of the invention ") In the steel according to the present invention, in consideration of the maximum achievable strength of the steel, although alloy elements other than c are not substantially important, these elements are required to provide The uniformity of the entire thickness of the required microstructure and the thickness of the steel plate greater than about 2.5 cm (1 inch) and the cooling rate range required for processing elasticity are important because the actual thickness in the middle part of the thick steel plate The cooling rate is lower than the surface, so the microstructure on the surface and in the middle can be quite different, unless the sensitivity of the steel to the difference in cooling rate between the surface of the steel plate and the middle part is eliminated. In this consideration, Mn and Mo alloy additives, and especially The combination of Mo and B is particularly effective. In the present invention, these additives are optimized in consideration of hardenability, weldability, low DBTT, and cost. As described earlier in this patent specification, from the viewpoint of reducing DBTT, The total amount of BCC alloy additives must be kept to a minimum, and better chemical standards and ranges must be set to meet these and other requirements of the present invention. (3) Low heat input Superior weldability Printed by the Consumer Cooperative of the Central Bureau of Standards of the Ministry of Economic Affairs (read the back note ^^ before filling out this page) The steel of the present invention is designed to have superior weldability, the most important Considerations, especially low heat input welding, is cold cracking or hydrogen cracking of coarse-grained HAZ. It has been found that the cold cracking sensitivity of the steel of the present invention is decisively affected by the carbon content and the HAZ microstructure form, rather than the prior art It is considered as the decisive parameter of hardness and carbon equivalent. When the steel is welded without or with low preheating (less than about 100 t (2 1 2 T)), in order to avoid cold cracking, a better carbon is added. The upper limit of the amount is about 0.1% by weight. As used herein, the present invention is not limited in any way. "Low heat input welding" refers to an arc energy of at most about 2 5 kilojoules per millimeter. Standard (CNS) A4% (210x297) #-21-Printed by A7 __ H7 of the Consumer Cooperatives of the Central Bureau of Standards of the Ministry of Economic Affairs 5. Description of the invention 彳 9) ears / mm) (7.6 kilojoules / inch) Welding Ductile iron or automatic tempering strip Asada loose iron microstructure provides superior cold cracking resistance. The other alloy elements in the steel of the present invention are carefully balanced and proportioned to the requirements of hardenability and strength, making the HAZ in coarse grained The required microstructures are formed. Role of alloying elements in steel blocks The role of various alloying elements of the present invention and the preferred concentration limits are explained below: Carbon (C) is one of the most effective strengthening elements in steel, and it can also be used with Strong carbide formers in steel, such as Ti, Nb, V, and Mo, combine to provide particle growth inhibition and precipitation strengthening during tempering, and carbon can also promote hardenability, that is, in steel during cooling A harder and stronger microstructure is formed. If the carbon content is less than about 0.04% by weight, it is not sufficient to cause the required strengthening in the steel, that is, a tensile strength greater than 830Mpa (120 ksi). If the carbon content is greater than about 0.1 2 % By weight, the steel is easily cold cracked during welding, and the toughness of the steel plate and its HAZ is reduced during welding, and the carbon content is preferably about 0. ◦ 4% by weight to about 0.12% by weight to produce the required The upper limit toughening iron, and carbon content of HAZ microstructure, i.e. automatic back scattered cremation article lesser amounts of iron and martensite is more preferably about 0.07 wt%. Manganese (M η) is a matrix strengthening agent in steel materials and can also strongly promote hardening. In order to obtain the required strength in steel plates with a thickness of more than about 2.5 cm (1 inch), the minimum amount is preferably 0 5% by weight Μ η And at least about the paper size applies to the Chinese national standard (CNS) Λ4 «1 phase U10X297 public potential) mV t ^ in n ^^^^ 1 ^^^^ 1 ^^^^ 1 ^^-^ 1 ^^ ^^ 1 (Please read the precautions on the back #Fill,? Ξ 本 i) -22- A7 _____H7 V. Description of the invention) 1.0 The minimum amount of Mn is better, but too much Mn is harmful to toughness. Therefore, the preferred upper limit of the present invention is about 2.5% by weight Μ η. This upper limit is also more suitable to substantially minimize central line segregation, which easily occurs at high η and continuous casting of the material and the entire thickness of the accompanying microstructure. For non-uniformity and properties, the upper limit of the Mn content is more preferably about 1.8% by weight. If the nickel content is increased by about 3% by weight, the required high strength can be achieved without adding manganese. Therefore, in a broad sense, It is preferably at most about 2.5% by weight. Silicon (S i) can be added to steel for the purpose of deoxidation, and the minimum amount for this purpose is about 0.01% by weight, but Si is a strong BCC stabilizer and therefore increases DB TT and has a negative impact on toughness For these reasons, when Si is added, the upper limit is preferably about 0.5% by weight Si, and when Si is added, the upper limit of the Si content is more preferably about 0.1% by weight, and deoxidation is not necessarily Silicon is required because aluminum or titanium can perform the same function. Printed by the Men ’s Consumer Cooperative of the Central Bureau of Standards of the Ministry of Economic Affairs (please read the precautions before filling this page) The addition of niobium (N b) is to promote the refining of the microstructure of the steel sheet after rolling, which can simultaneously improve the strength and Toughness, precipitation of niobium carbides and carbonitrides during hot rolling can prevent recrystallization and inhibit particle growth, so it provides Vostian iron particle refining, and precipitation of niobium carbides and carbonitrides during tempering can provide all Secondary hardening is required to compensate for the strength loss typically observed in tempering above about 500 ° C (930 ° F), for these reasons, at least about 0.02 wt% Nb is preferred, and At least about 0.03 wt% Nb is more suitable, but Nb is a strong BCC stabilizer and therefore can increase DBTT. Too much Nb is detrimental to weldability and HAZ toughness, so a maximum amount of about 0.1 wt% is better. The upper limit of Nb content is more suitable for the Chinese paper standard (CNS) Λ4 specification (210x297 male i) -23- Printed by the Consumer Cooperatives of the Central Standards Bureau of the Ministry of Economic Affairs A7 137 V. Description of the invention h) about 0.05 weight%. Vanadium (V) is sometimes added to obtain precipitation strengthening. Vanadium carbides and carbonitride fine particles are formed in HA Z during tempering in steel and after cooling after welding. When dissolved in Vostian iron, V is Hardening has a strong benefit. When V is added to the steel of the present invention, at least about 0.02% by weight V is preferred, but excessive V will promote cold cracking during welding and is harmful to the toughness of the matrix steel and its HAZ. Therefore, the addition of V is preferably limited to a maximum of about 0.1% by weight, and more preferably limited to a maximum of about 0.05% by weight. Titanium (T i), when added in a small amount, can effectively form titanium nitride (T i N) particles, After rolling the steel, the structure and HAZ can refine the particle size. Therefore, the toughness of the steel can be improved. The addition amount of τ i is such that the weight ratio of Ti / N is preferably about 3.4. Ti is a strong BCC. Stabilizers and therefore can increase DBTT, too much Ti is not good for toughness by forming coarser T i N or titanium carbide (T i C) particles, and Ti content below about 0.008% by weight usually does not provide sufficiently fine particles 〇3 重 The size or connection of N in the steel to form T i N, and is greater than about 〇3 重The amount% can cause the toughness to deteriorate, and the steel more preferably contains at least about 0.01% by weight and not more than about 0.02% by weight. Aluminum (A 1) is added to the steel of the present invention for the purpose of deoxidation. At least about 0.001 wt. 1 is more suitable for this purpose, and more preferably at least about 0.005% by weight. Nitrogen in HAZ, but A 1 is a strong BCC stabilizer and therefore increases DBTT. If the content of A 1 is too high, that is, higher than about 0/0 5 The paper size applies the Chinese national standard {CNS) 4 specifications (210X 297 public power)-^^^ 1 In m I m- ^. (诮 Please read the precautions on the back before filling in this page) -24- Λ7 _ 五 7 5. The invention description such as) The amount%, tends to form alumina The (A 1 2 0 3) type blend is liable to be detrimental to the toughness of steel and HAZ. The upper limit of the A 1 content is more preferably about 0.33% by weight. Molybdenum (Μ 〇) can increase the hardenability of the steel during direct quenching, especially in combination with boron and niobium. Μ 〇 can also provide fine 〇 2 C carbides, which can promote secondary when the steel is tempered Hardened, preferably at least about 0.1 wt% Mo, and more preferably at least about 0.2 wt% Mo, but,

Mo爲強烈的BCC安定劑且因此增加DBTT，過量的 Mo將促成熔接時的冷裂化，同時也容易惡化鋼材及 HAZ之韌性，所以最高較宜約〇.8重量％，且最高約 ◦ . 5重量％更佳。 鉻（C r )在直接淬火時有增加鋼材可硬化度之傾向 ，其也可提供抗腐蝕性及抗氫引發之裂化（Η I C ),與 Μ 〇類似，過量的C 1：將促成熔接時冷裂化之傾向，同時 也容易惡化鋼材及其H A Ζ之韌性，所以當添加C r時， 最高較宜的1.0重量％Cr,更宜當添加Cr時，Cr 含量約0.2重量％至約0.6重量％。 經濟部中央樣隼局負工消費合作社印製 (請先閱讀背而之注意事項再填寫本頁) 鎳（N i )爲本發明鋼材尤其是在HA Z得到所需 DBTT之重要合金添加物，其爲鋼材中最強的FCC安 定劑之一，N i添加至鋼材中可強化交叉滑動且因此可降 低DBTT，雖然與Μη及Mo添加物之程度不同，Ni 添加至鋼材中也可提昇可硬化度，且因此可增加厚部份（ 厚度大於約2 . 5公分（1吋））之微結構整個厚度均勻 性及性質，爲了在熔接的HAZ中得到所需的DBTT, 本紙張尺度適用中國國家栳準（CNS ) A4規格{ 210X 297公焓} -25- A7 Η 7 459052 五、發明説明h ) 最少的N i含量較宜約1 . 0重量％，更宜約1 . 5重量 %，因爲Ni爲昂貴的合金元素，鋼材中的Ni含量較宜 低於約3.0重量％，更宜低於約2.5重量％,又更宜 低於約2.0重量％，且再更宜低於約1,8重量％，以 實質上降低鋼材之成本。 銅（C u )爲有用之合金添加物，可經由ε —銅沈澱而 在回火時提供硬化，爲了此目的較宜至少加入約〇 . 1重 量％，更宜至少加入約0 . 5重量％的（：11，Cu也是鋼 材中的FCC安定劑，可少量降低DBTT, Cu也有益 於抗腐蝕及HI C，在較高含量時，Cu引發過量沈澱硬 化並可降低韌性及同時提高鋼板及HAZ之DBTT,較 高含量的Cu也可在板塊鑄造及熱輥軋時促成脆化，需要 Ni之輔助添加物供緩和，基於上述理由，Cu上限較宜 爲約1 · 5重量％，且上限爲約1 . 0重量％更佳。 硼（B )在少量時可大幅增加鋼材之可硬化性及促進 形成條麻田散鐡鋼材之微結構，經由抑制上變韌鐵在鋼板 及粗粒化H A Z形成，減少變韌鐵及肥粒鐵，通常，此目 的需要至少約0 . 0004重量％B，當硼添加至本發明 之鋼材時，較宜約0 . 0006重量％至約0 . 0020 重量％，且上限爲約0.0010重量％更佳，但是，如 果鋼材中的其他合金可提供適當的可硬化性及所需的微結 構時，不需要加入硼。 本發明鋼材中的這些性質組合，提供低成本之技術供 某些低溫操作，例如在低溫下儲存及輸送天然氣，與—般 本紙張尺度適用中國國家標準（CNS ) Λ4規格（210X297公# ) n m HD ^^^1 ^^^1 一eJ _ _ (諳先閱讀背面之注意事項再填寫本頁) 經濟部中央標準局負工消费合作社印聚 -26- 經濟部中央標準局員工消费合作社印製 4 b ^ i' - A7 B? 五、發明説明) 需要更高鎳含量（至多約9重量％)且更低強度（低於約 830Mpa (120ksi)之目前先進的商業化供應 鋼材比較，這些新的鋼材可提供明顯的材料節省供低溫應 用，化學及微結構設計可用於降低DBTT及在厚度大於 約2 . 5公分（1吋）之整個厚度中提供均勻的機械性質 ，這些新鋼材之鎳含量較宜低於約3重量％，張力強度大 於830Mpa (120ks i)，較宜大於約860 Mpa (125ksi)，且更宜大於約900Mpa ( 130ks i)，延性轉脆溫度（DBTT)低於約 —73°C (- 100°F)，且在DBTT提供極佳的韌性 ，這些新的鋼材之張力強度可大於約93OMpa ( 135ks i),或大於約 965Mpa (14〇ks i )，或大於約lOOOMpa (145ks i)，這些鋼 材之鎳含量在必要時可增加至大於約3重量％以強化熔接 後的性質，每增加1重量％的鎳，預期可降低鋼材之 DBTT約l〇°C (18°F)，鎳含量較宜低於9重量％ ，更宜低於約6重量％，較宜使鎳含量最少化以減低鋼材 之成本。 雖然上述發明以一或多個具體實施例說明，必須了解 也可進行其他修改而沒有偏離本發明在下列申請專利範圍 中陳述之範圍。 名詞附錄 A =,轉化溫度： 加熱時開始形成變韌鐵之溫度； (請先閱讀背面之注意事項弄填寫本頁)Mo is a strong BCC stabilizer and therefore increases DBTT. Excess Mo will promote cold cracking during welding and also easily deteriorate the toughness of steel and HAZ. Therefore, the highest Mo is preferably about 0.8% by weight and the highest is about ◦. 5 % By weight is more preferred. Chromium (C r) tends to increase the hardenability of the steel during direct quenching. It can also provide corrosion resistance and resistance to hydrogen-induced cracking (Η IC). Similar to Μ〇, excess C1: will promote fusion. The tendency of cold cracking is also easy to deteriorate the toughness of steel and its HA AZ. Therefore, when C r is added, the most suitable 1.0% by weight Cr is more suitable. When Cr is added, the Cr content is about 0.2% by weight to about 0.6% by weight. %. Printed by the Central Cooperative Bureau of the Ministry of Economic Affairs, Consumer Cooperatives (please read the precautions before filling this page) Nickel (N i) is an important alloy additive for the steel of the present invention, especially the required DBTT in HA Z, It is one of the strongest FCC stabilizers in steel. Ni added to steel can strengthen cross-sliding and therefore reduce DBTT. Although it is different from Mn and Mo additives, Ni added to steel can also improve hardenability. , And therefore can increase the thickness uniformity and properties of the microstructure of the thick part (thickness greater than about 2.5 cm (1 inch)). In order to obtain the required DBTT in the welded HAZ, this paper size is applicable to the country of China 栳Standard (CNS) A4 specification {210X 297 enthalpy} -25- A7 Η 7 459052 V. Description of invention h) The minimum N i content is preferably about 1.0% by weight, more preferably about 1.5% by weight, because Ni As an expensive alloying element, the Ni content in the steel is preferably less than about 3.0% by weight, more preferably less than about 2.5% by weight, still more preferably less than about 2.0% by weight, and even more preferably less than about 1,8% by weight. % To substantially reduce the cost of steel. Copper (C u) is a useful alloying additive that can provide hardening during tempering through ε-copper precipitation. For this purpose, it is preferable to add at least about 0.1% by weight, more preferably at least about 0.5% by weight. (: 11, Cu is also an FCC stabilizer in steel, which can reduce DBTT by a small amount, Cu is also beneficial to corrosion resistance and HIC. At higher levels, Cu causes excessive precipitation and hardening, which can reduce toughness and improve steel and HAZ at the same time. DBTT, higher content of Cu can also promote embrittlement during block casting and hot rolling, and the auxiliary additive of Ni is needed to alleviate. Based on the above reasons, the upper limit of Cu is preferably about 1.5% by weight, and the upper limit is About 1.0% by weight is better. Boron (B) can greatly increase the hardenability of the steel and promote the formation of the microstructure of the Asada scattered steel in a small amount. By suppressing the toughening of iron, the formation of steel and coarse-grained HAZ is suppressed. , To reduce toughened iron and ferrous iron, usually, this purpose requires at least about 0.004 wt% B, when boron is added to the steel of the present invention, it is more preferable to be about 0.006 wt% to about 0.020 wt%, The upper limit is more preferably about 0.0010% by weight, but, for example, Other alloys in steel can provide proper hardenability and required microstructure without the need to add boron. The combination of these properties in the steel of the present invention provides a low-cost technology for certain low temperature operations, such as storage at low temperatures And transmission of natural gas, and-this paper size applies Chinese National Standards (CNS) Λ4 specifications (210X297 公 #) nm HD ^^^ 1 ^^^ 1 eJ _ _ (谙 Please read the precautions on the back before filling this page ) Printed by the Central Standards Bureau of the Ministry of Economic Affairs, Consumer Cooperatives 26-Printed by the Consumers Cooperative of the Central Standards Bureau of the Ministry of Economic Affairs 4 b ^ i '-A7 B? 5. Description of the invention) Need for higher nickel content (up to about 9% by weight) ) And lower strength (compared with current advanced commercial supply steels below about 830Mpa (120ksi), these new steels can provide significant material savings for low temperature applications, chemical and microstructure design can be used to reduce DBTT and Provide uniform mechanical properties throughout the thickness of about 2.5 cm (1 inch). The nickel content of these new steels is preferably less than about 3% by weight, and the tensile strength is greater than 830Mpa (120ks i), and more preferably greater than about 860. Mpa (125ksi), and more preferably about 900Mpa (130ks i), ductility to brittle temperature (DBTT) below about -73 ° C (-100 ° F), and provide excellent toughness in DBTT, these new steels The tensile strength can be greater than about 93OMpa (135ks i), or greater than about 965Mpa (14〇ksi), or greater than about 100OMpa (145ksi). The nickel content of these steels can be increased to greater than about 3% by weight if necessary to strengthen The properties after welding are expected to reduce the DBTT of the steel by about 10 ° C (18 ° F) for each 1% by weight of nickel. The nickel content is preferably less than 9% by weight, and more preferably less than about 6% by weight. It is desirable to minimize the nickel content to reduce the cost of steel. Although the above invention is illustrated in one or more specific embodiments, it must be understood that other modifications may be made without departing from the scope of the invention as set forth in the scope of the following patent applications. Appendix A to Nouns, Conversion temperature: Temperature at which toughened iron starts to form when heated; (Please read the precautions on the back to fill out this page)

本紙張尺度適用中國國家標準（CNS ) A4规梠（210X297公# ) -27- A7 B7 五、發明説明^ Ah轉化溫度： Ah〇3： An轉化溫度： BCC: 冷卻速率： 加熱時完成將肥粒鐵形成沃斯田鐵之溫 度； 氧化鋁； 冷卻時沃斯田鐵開始轉化成肥粒鐵之溫 度； 體心立方； 在鋼板厚度中心或實質中心之冷卻速率； CRSS(臨界變形剪應鋼材之一種本質性質，敏感於變形時， 力）： 低溫： DBTT (延性轉脆溫 度）： 經濟部中央標準局貝工消費合作社印聚 FCC: 粒子： 粒子界面 硬化粒子 HAZ: 位移可交叉滑移之容易性，也就是說較 容易交叉滑移之鋼材也將有較低的CRSS 及因此較低的DBTT; 低於約-40 °C (-40 T)之任何溫度； 描述結構鋼材中的兩個裂斷部份；在低於 DBTT之溫度，傾向於發生低能劈開（脆 化）之損壞，但在高於DBTT之溫度，傾 向於發生高能延性劈開之損壞； 面心立方； 在多晶材料中的個別晶體； 金屬中相對於從一個結晶態方向轉化成 另一種時之狹窄區域，因此將粒子彼此 分離； 一或多種的ε-銅、M02C、或銀及銳之碳 化物與碳氮化物 熱影響區域： (請先閱讀背面之注意事項再填寫本頁) ." 訂 本紙張尺度適用中國國家榇準（CNS ) Λ4現枯（210X 297公犛） -28- A7 B7 經濟部中央標準局員工消費合作社印裂 五、發明説明) HIC: 氫引發的裂斷： 高角晶界： 分隔兩個結晶向差異大於約8°之相鄰粒 子的粒子界面 HSLA: 高強度，低合金： 嚴苛重複加熱： 加熱（或再度加熱）至約Au轉化溫度至約 Au轉化溫度之溫度； 低合金鋼材 含鐵及低於約10重量％總合金添加物之 鋼材； 低熱輸入熔接： 電弧能量至多約2.5千焦耳/毫米（7.6千 焦耳/吋）之熔接； MA: 麻田散鐵-沃斯田鐵； M02C: 鉬碳化物之一種形式； Ms轉化溫度： 冷卻時，沃斯田鐡開始轉化成麻田散鐵 之溫度； 主要： 在本發明中指至少約50體積％; 前沃斯田鐵粒子大 熱輥軋鋼扳在沃斯田鐵不會再結晶化溫 小： 度之溫度範圍下輥軋前，平均沃斯田體 粒子大小； 淬火： 在本發明中用於描述以任何方法加速冷 卻，其中使用可增加鋼材冷卻速率之液 體，與空氣冷卻相反； 淬火停止溫度 停止淬火後，由於熱從鋼板厚度中心傳 (QST): 送而使鋼板表面達到的最高或實質上最 高之溫度； 本紙張尺度適用中國國家標準（CNS)A4規梢（210X297公# ) (請先閱讀背面之注意事項再填寫本頁) 訂 29 - A7 Η 7 五、發明説明心） 經濟部中央標準局貝工消費合作社印製 板塊： 任何大小之鋼材塊； Sv： 鋼板每單位體積高角晶界之總界面面積 張力強度： 在張力測試中 ，最大荷重對原先截面積 之比例； TiC: 碳化鈦； TiN: 氮化鈦； T n r溫度： 低於此溫度， 沃斯田鐵不會再結晶化； TMCP: 熱機械控制輥軋處理。 ("先閱讀背面之注意事項再填涔本頁) 本紙張尺度適用中國國家榇準（CNS ) A4规桔（210X297公嫠） -30-This paper size applies the Chinese National Standard (CNS) A4 Regulation (210X297 公 #) -27- A7 B7 V. Description of the Invention ^ Ah Conversion Temperature: Ah〇3: An Conversion Temperature: BCC: Cooling Rate: Finish the fertilizer when heating Temperature at which granular iron forms Vosstian iron; alumina; temperature at which Vosstian iron begins to transform into ferrous iron at cooling; body-centered cubic; cooling rate at the thickness center or substantial center of the steel plate; CRSS (critical deformation shear steel An essential property, which is sensitive to deformation, force): Low temperature: DBTT (ductility to brittleness temperature): Printed by the Central Standards Bureau of the Ministry of Economic Affairs, Shellfisher Consumer Cooperative, FCC: Particles: Particle interface hardened particles, HAZ: Displaceable cross slip Ease, meaning that steels that are more likely to cross-slip will also have lower CRSS and therefore lower DBTT; any temperature below about -40 ° C (-40 T); describe two of the structural steels Fractured parts; at temperatures below DBTT, tend to occur low-energy cleavage (embrittlement) damage, but at temperatures above DBTT, tend to occur high-energy ductile cleavage damage; face-centered cubic; in polycrystalline materials Individual crystals; narrow regions in the metal relative to the transition from one crystalline state to another, thus separating the particles from one another; one or more of ε-copper, M02C, or silver and sharp carbides and carbonitrides thermal effects Area: (Please read the precautions on the back before filling this page). &Quot; The size of the paper used in the edition is applicable to the Chinese National Standards (CNS) Λ4 is now dry (210X 297 public) -28- A7 B7 Employees of the Central Standards Bureau of the Ministry of Economic Affairs Consumption Cooperative Coupling V. Description of the invention) HIC: Hydrogen-induced cracking: High-angle grain boundary: Particle interface separating two adjacent particles with a crystal orientation difference greater than about 8 ° HSLA: High strength, low alloy: Severe repeated heating : Heating (or reheating) to a temperature ranging from about Au conversion temperature to about Au conversion temperature; steels with low alloy steel containing iron and less than about 10% by weight of total alloy additions; low heat input welding: arc energy up to about 2.5 kilojoules / Mm (7.6 kilojoules / inch) welding; MA: Asada loose iron-Vosstian iron; M02C: a form of molybdenum carbide; Ms conversion temperature: Voss tincture begins when cooling The temperature at which it is converted into Asada scattered iron; Mainly: In the present invention means at least about 50% by volume; the former Vostian iron particle hot rolling steel is rolled under the temperature range where Vostian Iron will not recrystallize. Before rolling, average particle size of Voss field; quenching: used in the present invention to describe accelerated cooling by any method, in which a liquid that can increase the cooling rate of steel is used, as opposed to air cooling; the quenching temperature is stopped due to heat after quenching From the center of the thickness of the steel plate (QST): The highest or substantially the highest temperature reached by the surface of the steel plate; This paper size applies the Chinese National Standard (CNS) A4 regulations (210X297 公 #) (Please read the precautions on the back first Refill this page) Order 29-A7 Η 7 V. Inventive Notes) Printed by the Central Standards Bureau of the Ministry of Economic Affairs, Shellfish Consumer Cooperatives: Plates of any size; Sv: Total interfacial area tension of high angle grain boundaries per unit volume of steel plate Strength: The ratio of the maximum load to the original cross-sectional area in the tensile test; TiC: titanium carbide; TiN: titanium nitride; T nr temperature: below this Degree, austenite does not recrystallize; TMCP: thermo-mechanical controlled rolling processing. (" Read the precautions on the back before filling this page) This paper size is applicable to China National Standard (CNS) A4 standard orange (210X297) -30-

Claims (1)

六、申請專利範圍 附件A : 第871 09691號專利申請案 (請先閲婧背面之注意事項再填荈本育) 中文申請專利範圍修正本 民國89年10月修正 1 . 一種製備鋼板之方法，該鋼板在該基質鋼板及其 HAZ 之 DBTT 都低於- 73°C(-100°F)，且張 力強度大於83〇Mpa (120ksi)，又其微結構 主要含回火化的微細粒化條麻田散鐵、回火化的微細粒化 低變韌鐵或其混合物|該方法之步驟包括： (a )將鋼板塊在（i )夠高到實質上均勻化該鋼板 塊且實質上溶解該鋼板塊中鋸及釩之全部的碳化物及碳氮 化物，及（i i )夠低到在該鋼板塊中建立大小低於 1 2 0微米之微細的初沃斯田鐵粒子之再加熱溫度下加熱 » (b )在沃斯田鐵再結晶的第一個溫度範圍下，在一 或多個熱輥軋通道下，減縮該鋼板塊形成鋼板； 經濟部智总財"局員工消骨合作社印製 (C )在低於T u r溫度但高於Α Γ 3轉化溫度的第二 個溫度範圍下，在一或多個熱輥軋通道下進一步減縮該鋼 板： - (d )在每秒1 0 t至每秒4 CTC〔 1 8 °F /秒一 7 2 T/秒）之冷卻率下使鋼板淬火至低於M s轉化溫度 加上2 0 0 °C ( 3 6 0 Τ )之淬火停止溫度： (e )停止該淬火；及 (f)在400°C (752°F)至AsL轉化溫度之回 表紙張反度通用中國國家樣隼（CNS ) A4規格（210X 297公釐_) . 1 ~ AS B8 CS D8 六、申請專利範圍 火溫度下使該鋼板回火足夠的時間，使硬化的粒子沈澱， 促使該鋼板之該微結構轉化成主要含回火化的微細粒化條 麻田散鐵、回火化的微細粒化低變韌鐵或其混合物。 2 .如申請專利範圍第1項之方法，其中該步驟（a )之再加熱溫度爲955°(：至1065 1(1750下-1 9 5 Q T )。 3 .如申請專利範圍第1項之方法，其中在步驟（b )發生之該鋼板塊厚度縮減爲3 0%至7 0%。 4 .如申請專利範圍第1項之方法，其中在步驟（c )發生之該鋼板厚度縮減爲4 0%至8 0%。 5 .如申請專利範圍第1項之方法’在步驟（f )回 火該鋼板前，另外還包括使該鋼板從該淬火停止溫度以空 氣冷卻至室溫之步驟。 6 .如申請專利範圍第1項之方法，其中步驟（a ) 之鋼板塊含鐵及下列重量％所示之下列合金元素： 0.04% 至 0.12%C， 1 % 至 9 % N 1 ， ---------衣------ΐτ (锖先閲讀背面之注意事項再填寫本頁) 經濟部智.^財,415员工;-«费合作社印製 ο ο ο 0 0 0 7 ，，b u ο N CM% % % 1 5 8 . . ο 1 o 至 至至% % % 2 及 i .—- N ΤΑ% % % 5 3 5 0 ο ο ο ·*· ο ο ο 至至至 % % % 00 Ον! ο ο ο ο ο ο 含 塊 板 鋼 該 中 其 法 方 之 項 6 第 圍 範 Mu 手 專 請 甲 如 A S N C 箪 樣 家 國 國 中 用 適 度 尺 I* 紙 ¥ 1公一97 2 ABC0 ^ Δ59052 經濟部%.¾財沌局員工消費合作社印製 "T\ 、 申請專利範圍 1 1 低於 6 重 量 % N 1 〇 1 8 如 串 請 專 利 範 圍 第 6 項 之 方 法 其 中 該 鋼 板 塊含 1 低 於 3 重 里 % N i 且 另 外 含 0 5 重 量 % 至 2 5 重量 /—ν 谙 1 I 先 1 % Μ η 〇 閲 讀 I | 9 如 串 請 專 利 範 圍 第 6 項 之 方 法 其 中 該 鋼 板 塊另 η 面 之 1 t t 外 含 至 少 — 種 培 白 下 列 之 添 加 物 ( ) 至 多 1 0 重量 注 意 華 [ 1 % C r ( 1 ) 至 多 0 5 重 量 % S 1 ( 1 1 )至 項 再 1 多 0 1 重 量 % V 1 及 ( i V ) 至 多 2 5 重 里 % Μ η ° % 本 永 頁 i 1 0 如 串 請 專 利 範 圍 第 6 項 之 方 法 其 中 該 鋼 板塊 1 另 外 含 0 0 0 0 4 重 量 % 至 0 0 0 2 0 重 量 % Β 0 i 1 1 1 如 甲 s主 S円 專 利 範 圍 第 1 項 之 方 法 » 其 該 鋼 板在 1 1 步 驟 ( f ) 回 火 後 1 實 質 上 含 1 0 0 % 回 火 化 的 微 細 粒化 訂 I 條 麻 田 散 鐵 〇 1 1 1 2 — 種 鋼 板 在 該 鋼 板 及 其 Η A Z 之 D B Τ Τ都 1 1 低於 一 7 3 °c ( — 1 0 0 T ) 張 力 強 度 大 於 8 3 0 ! ! Μ Ρ a ( 1 2 0 k S 1 ) 微 結 構 主 要 含 回 火 化 的 微 細粒 i 化 條 麻 田 散 鐵 回 火 化 的 微 細 粒 化 低 變 韌 鐵 或 其 混 合 物， 1 1 且 其 中 該 鋼 板 是 從 再 度 加 熱 鋼 板 Lf4rt 塊 製 造 該 鋼 板塊含 鐵及 1 1 下 列 重 量 % 所 示 之 下 列 口 金 元 素 1 1 0 - 0 4 % 至 0 1 2 % C > i 1 1 % 至 9 % N 1 1 | 0 * 1 % 至 1 5 % C U » 1 1 〇 * 1 % 至 0 8 % Μ 0 » 1 1 0 * 0 2 % 至 0 1 % Ν b ) 1 ! 1 表紙張尺度適用中國國家橾窣（CNS ) Μ規格（2tOX 29?公釐）-3 - G 52 A 8 B8 C8 D8 六、申請專利範圍 0.008% 至 0·03%Τι， 0. 001% 至 0.05% A 1，及 0 . 002%至 0 005%N。 1 3 .如申請專利範圍第1 2之鋼板，其中該鋼板塊 含低於6重量％ N i 。 1 4 .如申請專利範圍第1 2項之鋼扳，其中該鋼板 塊含低於3重量％Νι·且另外含約〇.5重量％至 2 . 5 重量 ％ Μ η。 1 5 .如申請專利範圍第1 2項之鋼板，其中該鋼板 塊另外含至少一種選自下列之添加物：（1 )至多1 . 0 重量％Cr ，（1 1)至多 〇. 5 重量％Si ，（1 1 i )至多0 . 1重量，及（iv)至多2 . 5重量％ Μη ° 1 6 .如申請專利範圍第1 2項之鋼板，其中該鋼板 塊另外含0 . 0〇〇4重量％至◦ . 0 02 ◦重量。 1 7 · —種供得到鋼板H A Ζ之D Β Τ Τ低於—7 3 (請先閲讀背1&之注意事項再填寫本頁) 丁 '-α 經.濟部智.¾財4Ag(工消費合作社印製 量 重 ο 加 .添 1 少 少減 至上 加質 添實 由且 經’ 係 U 其 C ，% 。 法量成 方重達 之 1 而 ) 素 OFO 元 ο 少化 ο 至定 1 及安 | 1 (N C P%B 夂紙張尺度適用中國國家標準（CNS ) Α4規格（210X297公釐）-4 -6. Appendix A of the scope of patent application: Patent application No. 871 09691 (please read the notes on the back of Jing before filling in this book) Chinese application for patent scope amendment October, 1989 Amendment 1. A method for preparing steel plates, The DBTT of the steel plate in the matrix steel plate and its HAZ are both lower than -73 ° C (-100 ° F), and the tensile strength is greater than 8300Mpa (120ksi), and its microstructure mainly contains tempered micronized grains. Loose iron, tempered micro-granulated low-toughness iron or mixtures thereof | the steps of the method include: (a) raising the steel block at (i) high enough to substantially homogenize the steel block and substantially dissolving the steel block All carbides and carbonitrides of the middle saw and vanadium, and (ii) heating at a reheating temperature low enough to create fine primary Vostian iron particles with a size of less than 120 microns in the steel block » (b) In the first temperature range of Vosstian Iron recrystallization, the steel block is reduced to form a steel plate under one or more hot rolling channels; (C) at a temperature lower than T ur but higher than A Γ 3 conversion temperature In the second temperature range, the steel sheet is further reduced under one or more hot-rolling channels:-(d) between 10 t / s and 4 CTC per second [1 8 ° F / s-7 2 T / s ) At a cooling rate of less than M s transformation temperature plus a quenching stop temperature of 200 ° C (360 ° T): (e) stop the quenching; and (f) at 400 ° C (752 ° F) to AsL conversion temperature, the reversion of the paper is the same as the general Chinese National Sample (CNS) A4 specification (210X 297 mm_). 1 ~ AS B8 CS D8 6. Scope of patent application Temper the steel sheet at fire temperature Sufficient time to precipitate the hardened particles, and promote the microstructure of the steel sheet to be transformed into tempered micro-granulated strip Asada loose iron, tempered micro-granulated low-toughened iron, or a mixture thereof. 2. The method according to item 1 of the scope of patent application, wherein the reheating temperature of step (a) is 955 ° (: to 1065 1 (under 1750-1 9 5 QT). 3. The method according to item 1 of scope of patent application A method in which the thickness of the steel plate in the step (b) is reduced to 30% to 70%. 4. The method according to item 1 of the patent application scope, wherein the thickness of the steel plate in the step (c) is reduced to 4 0% to 80%. 5. The method according to item 1 of the scope of patent application 'before step (f) tempering the steel sheet, the method further includes the step of cooling the steel sheet from the quenching stop temperature to air to room temperature. 6. The method according to item 1 of the scope of patent application, wherein the steel block of step (a) contains iron and the following alloying elements shown by the following weight%: 0.04% to 0.12% C, 1% to 9% N 1,- ------- Clothing ------ ΐτ (锖 Please read the notes on the back before filling in this page) Ministry of Economic Affairs, wise, 415 employees;-«Printed by the cooperative ο ο ο 0 0 0 7, bu ο N CM%%% 1 5 8.. Ο 1 o to to%%% 2 and i .-- N ΤΑ%% 5 3 5 0 ο ο ο ο ο ο ο to To%%% 00 Ον! Ο ο ο ο ο ο Including the sheet steel, the method of which is 6 of the law. Mu hand-specially invites a person such as ASNC to use a moderate ruler I * paper for each country and country. ¥ 1 male-97 2 ABC0 ^ 590590 Ministry of Economic Affairs%. Printed by the Bureau ’s Consumer Cooperatives " T \, Patent application scope 1 1 less than 6% by weight N 1 〇 1 8 If the method of item 6 of the patent scope is stringed, the steel block contains 1 less than 3% by weight N i and In addition, 0 5 wt% to 2 5 wt / —ν 谙 1 I first 1% Μ η 〇Read I | 9 If the method of item 6 of the patent scope is stringed, wherein the steel plate has 1 tt on the other side of the steel plate and contains at least— Add the following additives () at most 10 weight. Attention Hua [1% C r (1) at most 0 5 weight% S 1 (1 1) at most 1 more 0 1 weight% V 1 and (i V) Up to 2 5% of the weight% Μ η °% This permanent page i 1 0 If the string please patent the 6th item The method in which the steel plate block 1 additionally contains 0 0 0 0 4 wt% to 0 0 0 2 0 wt% Β 0 i 1 1 1 is the method of the first item in the scope of the patent of the main patent S »The steel plate is in step 1 1 (f) After tempering, 1 essentially contains 100% tempered fine-grained steel. I. Asada loose iron. 0 1 1 1 2 — The steel plate in this steel plate and its Η AZ DB Τ Τ are all 1 1 below 1 7 3 ° c (— 1 0 0 T) Tensile strength is greater than 8 3 0!! Μ Ρ a (120 k S 1) The microstructure mainly contains tempered fine grains. Granulated low-toughness iron or a mixture thereof, 1 1 and wherein the steel plate is manufactured from a reheated steel plate Lf4rt block, the steel block contains iron and 1 1 the following gold elements shown in the following weight% 1 1 0-0 4% to 0 1 2% C > i 1 1% to 9% N 1 1 | 0 * 1% to 15% CU »1 1 〇 * 1% to 0 8% Μ 0 »1 1 0 * 0 2% to 0 1% Ν b) 1! 1 The paper size is applicable to China National Cricket (CNS) Μ specifications (2tOX 29? Mm)-3-G 52 A 8 B8 C8 D8 6. The scope of patent application is 0.008% to 0.03% Tι, 0.001% to 0.05% A 1, and 0.002% to 0 005% N. 13. The steel plate according to claim 12 of the patent application range, wherein the steel plate block contains less than 6% by weight Ni. 14. The steel plate according to item 12 of the scope of patent application, wherein the steel plate block contains less than 3% by weight of Nm · and additionally contains about 0.5% by weight to 2.5% by weight of Mn. 15. The steel plate according to item 12 of the patent application scope, wherein the steel plate block additionally contains at least one additive selected from the following: (1) up to 1.0 wt% Cr, (1 1) up to 0.5 wt% Si, (1 1 i) at most 0.1 weight, and (iv) at most 2.5% by weight Mn ° 16. The steel plate according to item 12 of the patent application scope, wherein the steel plate block additionally contains 0.000. 4% by weight to ◦. 0 02 ◦ by weight. 1 7 · D B Τ Τ for obtaining steel plate HA TZ is lower than -7 3 (Please read the notes on back 1 & then fill out this page) Ding'-α Economy. Ministry of Economic Affairs. Consumption cooperatives print a lot ο increase. Add 1 to reduce the quality and increase the quality and reason, and the system is based on its C,%. The legal amount is equal to the weight of 1 and) The OFO element is reduced ο to definite 1 and safe | 1 (NCP% B 夂 paper size applies to Chinese National Standard (CNS) Α4 size (210X297 mm)-4-
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