TW200538561A - A high-strength thick steel plate excellent in low temperature toughness at heat affected zone resulting from large heat input welding - Google Patents

A high-strength thick steel plate excellent in low temperature toughness at heat affected zone resulting from large heat input welding Download PDF

Info

Publication number
TW200538561A
TW200538561A TW094110988A TW94110988A TW200538561A TW 200538561 A TW200538561 A TW 200538561A TW 094110988 A TW094110988 A TW 094110988A TW 94110988 A TW94110988 A TW 94110988A TW 200538561 A TW200538561 A TW 200538561A
Authority
TW
Taiwan
Prior art keywords
mass
welding
haz
toughness
steel plate
Prior art date
Application number
TW094110988A
Other languages
Chinese (zh)
Other versions
TWI295693B (en
Inventor
Minoru Ito
Akihiko Kojima
Masanori Minagawa
Yoichi Tanaka
Toshiei Hasegawa
Jun Otani
Original Assignee
Nippon Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Publication of TW200538561A publication Critical patent/TW200538561A/en
Application granted granted Critical
Publication of TWI295693B publication Critical patent/TWI295693B/en

Links

Classifications

    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/14Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/001Ferrous alloys, e.g. steel alloys containing N
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/002Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/005Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/06Ferrous alloys, e.g. steel alloys containing aluminium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/08Ferrous alloys, e.g. steel alloys containing nickel
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/12Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)

Abstract

The present invention provides a high-strength thick steel plate having a plate thickness of 50 to 80 mm and a tensile strength of 490 to 570 MPa which is able to realize an excellent HAZ toughness even when welding with a heat input of 20 to 100 kJ/mm is conducted and is characterized by containing, by wt%, 0.03-0.14% of C, 0.30% or less of Si, 0.8-2.0% of Mn, 0.02% or less of P, 0.005% or less of S, 0.8-4.0% of Ni, 0.003-0.040% of Nb, 0.001-0.040% of Al, 0.0010-0.0100% of N, and 0.005-0.030% of Ti, where Ni and Mn satisfy equation [1], and the balance of iron and unavoidable impurities: Ni/Mn ≥10×Ceq-3 (0.36 < Ceq < 0.42) [1] where, Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15.

Description

200538561 九、發明說明: 【發明所屬之技彳#領域】 技術領域 本發明係有關於一種被使用於船舶、海洋構造物、中 5南層大樓、橋樑等的焊接熱影響部(Heat Affected Zone,以 下稱為HAZ。)的低溫韌性優異之高強度厚鋼板,特別係有 關於一種鋼板,該鋼板係板厚5〇111111以上、母材拉伸強度 490〜570MPa級,且具有即使於進行焊接入熱量為 20〜100kJ/mm的焊接時亦優異的焊接接合部者。 10 【^^标】 背景技術 近年來,對於被使用於船舶、海洋構造物、中高層大 樓、橋樑等大型構造物的焊接用鋼材的材質特性之需求愈 趨嚴格。特別是於這些構造物中多使用板厚超過5〇mm厚且 15母材的拉伸強度為570Mpa級之鋼板。又,為了促進焊接的 效率化,於此高強度的厚鋼板的焊接上,對以電氣焊接法、 電熔渣焊接法等為代表的大入熱焊接法之丨回焊接進行檢 讨,與母材的韌性相同地,對HAZ韌性的要求亦愈趨嚴格。 注意到可適用大入熱焊接法的鋼材之HAZ韌性的提案 2〇到目刚為止數量相當多。例如,於曰本特公昭55-026164號 △報中係揭露一種藉著確保鋼中的微細的丁丨氮化物,使 AZ的’天斯田鐵晶粒縮小,使韋刃性提高之發明。又,於曰200538561 IX. Description of the invention: [Technical field #of the invention] Technical Field The present invention relates to a heat affected zone (Heat Affected Zone) used in ships, marine structures, middle and fifth-story buildings, bridges, etc. Hereinafter referred to as HAZ.) High-strength thick steel plates with excellent low-temperature toughness are particularly related to a steel plate having a plate thickness of 5010111 or more, a base material tensile strength of 490 to 570 MPa, and having a weldability of Welding joints that are excellent in welding with heat of 20 to 100kJ / mm. 10 [^^] Background Art In recent years, the demand for material properties of welding steel materials used in large structures such as ships, marine structures, high-rise buildings, and bridges has become more stringent. In particular, in these structures, a steel plate having a plate thickness of more than 50 mm and a tensile strength of 15 base materials of 570 MPa is often used. In addition, in order to promote the efficiency of welding, in the welding of this high-strength thick steel plate, the back welding of the large-scale heat welding method represented by the electric welding method, the electric slag welding method, and the like is reviewed. The toughness of the material is the same, and the requirements on the HAZ toughness are becoming stricter. It is noted that the number of proposals for HAZ toughness of steels to which the large-entry heat welding method can be applied is quite large up to the present. For example, in the Japanese newspaper No. 55-026164 of Yu Yue Ben, the invention of the △ newspaper discloses an invention that reduces the size of AZ Tiantian iron grains of AZ by improving the fine butyl nitride in the steel and improves the cutting edge. Also, Yu Yue

本特開平03-264614號公報中係提出一種將Ti氮化物與MnS 之複合析出物作為肥粒鐵之變態核加以有效利用,使haz 5 200538561 韌性提咼之發明。進而,於日本特開平04_143246號公報中 係提出-種將Ti氮化物與_之複合析出物作為晶界肥粒鐵 之析出核加以有效利用,使HAZ韌性提高之發明。The Japanese Patent Application Laid-Open No. 03-264614 proposes an invention in which a composite precipitate of Ti nitride and MnS is used as a metamorphic nucleus of fertilized iron to improve the toughness of haz 5 200538561. Furthermore, Japanese Patent Application Laid-Open No. 04_143246 proposes an invention in which a composite precipitate of Ti nitride and 作为 is effectively used as a nucleus of grain boundary fertilizer grain iron to improve the HAZ toughness.

但是,由於該Ti氮化物於與HAZ之最高溫度超過14〇〇 5 °c的焊接金屬的交界(以下亦稱為焊接結合部)附近幾乎會 固溶,故有使韌性提高效果降低的問題。因此,利用上述 的Ti氮化物的鋼材不易達到近年來對HAZ_性的嚴格的要 求及超大入熱焊接上必要的HAZ動性之特性。 作為改善該焊接結合附近的韌性之方法有將含有丁1氧 10化物的鋼使用於厚板、型鋼等各種領域上。例如,於厚鋼 板的領域中有日本特開昭61-079745號公報及日本特開昭 61-117245號公報中記載的發明,含有丁丨氧化物的鋼對大入 熱焊接部的韌性提高非常有效,可適用於高張力鋼。其原 理為,以即使於鋼的融點亦安定的!^氧化物作為析出位 15置’於焊接後的溫度降低途中析出Ti氮化物、MnS等,進 而以該Ti氮化物、MnS等作為位置生成微細的肥粒鐵,結 果可抑制對韌性有害的粗大肥粒鐵的生成,可防止勤性 劣化。 ' 但是,此Ti氧化物具有朝鋼中分散的個數無法很多的 2〇問題。其原因為Ti氧化物的粗大化及凝集體,若讓Ti氧化物 的個數增加,就會增加5//m以上的粗大的Ti氧化物,即所 謂的内含物。此5/zm以上的内含物會成為構造物破壞的起 點或引發韋刃性下降,由於相當有害,應該要避免。因此 為了達成HAZ韌性的提高,有必要有效利用不易產生粗大 6 200538561 化及/旋集體,可比Τι氧化物更微細地分散的氧化物。 又,该Τι氧化物朝鋼中的分散方法多為朝實質上不含 Α1等強脫氧兀素的溶鋼中添加Ή。但是,單純地僅於溶鋼 中添加Ti,不易控制鋼中的丁丨氧化物的個數、分散度,進一 5步亦不易控制TiN、馗沾等析出物的個數、分散度。因此, 於僅藉著Τι脫氧使Τι氧化物分散的鋼中,具有例如Ti氧化物 的個數不充份或厚板的板厚方向的勃性變動之問題。 針對此問題’於日本特開平〇心293937號公報及日本特 開平10-183295號公報中係揭露有一種藉著於添加Ή後添加 1〇 A1或同時添加A1、Ca,有效利用生成的Ti-Al複合氧化物或 Τι、A卜Ca的複合氧化物之發明。藉此,可使大入熱焊接 HAZ初性大幅提高。 C ;务明内】 發明揭示However, this Ti nitride almost solid-solves near the junction (hereinafter also referred to as the welded joint) with the weld metal whose maximum HAZ temperature exceeds 1405 ° C, so that there is a problem that the effect of improving toughness is reduced. Therefore, it is difficult for steel materials using the above-mentioned Ti nitrides to meet the stringent requirements for HAZ property in recent years and the characteristics of HAZ mobility necessary for ultra large heat welding. As a method for improving the toughness in the vicinity of the welded joint, a steel containing butyrate is used in various fields such as a thick plate and a shaped steel. For example, in the field of thick steel plates, there are inventions described in Japanese Patent Application Laid-Open No. 61-079745 and Japanese Patent Application Laid-Open No. 61-117245, and the toughness of steels containing butadiene oxide is greatly improved in the toughness of large-input heat-welded parts. Effective, suitable for high tension steel. The principle is to stabilize even the melting point of steel! ^ The oxide is placed as the precipitation position 15 and Ti nitrides, MnS, etc. are deposited on the way after the temperature decreases after welding, and the Ti nitrides, MnS, etc. are used as positions to generate fine ferrous iron, and as a result, coarseness that is harmful to toughness can be suppressed. The formation of fertilizer iron can prevent the deterioration of the duty. 'However, this Ti oxide has a problem of not being able to disperse much in steel. This is due to the coarsening and agglomeration of Ti oxides. If the number of Ti oxides is increased, coarse Ti oxides, which are referred to as inclusions, will increase by 5 // m or more. These inclusions above 5 / zm will be the starting point of structural damage or cause a decline in the edge sharpness. They should be avoided because they are quite harmful. Therefore, in order to achieve the improvement of the HAZ toughness, it is necessary to effectively use the oxide which is not easy to produce coarseness and / or spin mass, and which can be dispersed more finely than Ti oxide. In addition, the method for dispersing the Ti oxide in steel is to add rhenium to a molten steel that does not substantially contain strong deoxygenin such as A1. However, it is difficult to control the number and dispersion of butyl oxide in the steel simply by adding Ti to the molten steel, and it is also difficult to control the number and dispersion of precipitates such as TiN and hafnium in the next five steps. For this reason, in steels in which Ti oxides are dispersed only by Ti deoxidation, there are problems such as an insufficient number of Ti oxides or a change in the thickness direction of a thick plate. In response to this problem, Japanese Unexamined Patent Publication No. 293937 and Japanese Unexamined Patent Publication No. 10-183295 have disclosed a method in which, by adding 10A1 after addition of gadolinium or A1 and Ca at the same time, the Ti- The invention of Al complex oxide or Ti, A and Ca complex oxide. This can greatly improve the initial performance of large-scale heat welding HAZ. C; Wu Mingnei

但是’將HAZ的沃斯田鐵晶粒縮小或以析出物作為肥 粒鐵的變態核生成肥粒鐵的上述過去的方法中,為了確保 板厚50mm以上且母材強度的拉伸強度為49〇MPa以上,有 必要使合金元素增加,此時,由於焊接HAZ的硬度會上升, 门寺使早刃性劣化的]VIA(Martensite-Austenite constituent)的 2〇生成會變得明顯,故無法安定地確保例如於造船領域中的E 級(_2〇C保證)等充份的HAZ韌性。更不用說無法得到母材 強度的技伸強度為570MPa以上時所需要的HAZ韌性。 因此,本發明之目的係提供一種於大入熱焊接下的焊 接熱影響部的低溫韌性優異之高強度厚鋼板,該低溫韌性 7 200538561 優異的咼強度厚鋼板係板厚50〜80mm、母材拉伸強度 49〇~570MPa級的鋼板,且即使進行焊接入熱量 2〇~ 1 〇〇kJ/mm的焊接亦可實現優異的焊接ηaz勤性。 本發明者們發現藉著規定Ni添加量及Ni/Mn,可有利地 5 解決上述問題,進一步加以檢討後完成本發明,本發明之 要旨如下。However, in the above-mentioned conventional method of reducing the grain size of the Vostian iron of HAZ or using a precipitate as a metamorphic nucleation of ferrous iron to produce ferrous iron, the tensile strength for securing a plate thickness of 50 mm or more and a base metal strength of 49 MPa As mentioned above, it is necessary to increase the alloying element. At this time, the hardness of the welding HAZ will increase, and the temple will deteriorate the early edge properties. VIA (Martensite-Austenite constituent) 20 will become obvious, so it cannot be securely secured. For example, it has sufficient HAZ toughness in the E-class (-20 ° C guarantee) in the shipbuilding field. Not to mention that the HAZ toughness required when the strength of the base metal cannot be obtained when the tensile strength is 570 MPa or more. Therefore, an object of the present invention is to provide a high-strength thick steel plate having excellent low-temperature toughness in a welded heat-affected zone under large-entry heat welding. The low-temperature toughness 7 200538561 has an excellent concrete strength thick steel plate having a thickness of 50 to 80 mm, and a base material. A steel sheet with a tensile strength of 49-570 MPa grade can achieve excellent welding ηaz performance even when welding with a welding heat of 20-1000 kJ / mm. The present inventors have found that by specifying the amount of Ni and Ni / Mn, the above problems can be solved advantageously, and the present invention is completed after further review. The gist of the present invention is as follows.

(1) 一種於大入熱焊接下的焊接熱影響部的低溫韌性優異 之高強度厚鋼板,含有C: 0.03〜0.14質量%、Si : 0.30 質量%以下、Μη : 0.8〜2.0質量%、P : 〇·〇2質量%以下、 〇 S : 0.005 質量 % 以下、Α1 : 0.001 〜0.040 質量 %、Ν : 0.0010〜0.0100 質量 %、Ni ·· 0·8〜4·0 質量 %、Ti : 0.005〜0.030質量 %、Nb : 0.003〜0.040質量 %,且Ni與 Μη滿足下式〔1〕,即:(1) A high-strength thick steel plate with excellent low-temperature toughness in a welded heat-affected zone under large-input heat welding, containing C: 0.03 to 0.14 mass%, Si: 0.30 mass% or less, Mn: 0.8 to 2.0 mass%, P : 〇 · 〇2% by mass or less, 〇S: 0.005% by mass or less, A1: 0.001 ~ 0.040% by mass, N: 0.0010 ~ 0.0100% by mass, Ni ·· 0 · 8 ~ 4.0% by mass, Ti: 0.005 ~ 0.030 mass%, Nb: 0.003 to 0.040 mass%, and Ni and Mη satisfy the following formula [1], that is:

Ni/Mn^ 10xCeq-3(0.36&lt; Ceq&lt; 0.42) 〔1〕 5 但,Ceq = C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15 又,剩餘為鐵及不可避免之雜質。 (2) 如上述(1)記載之於大入熱焊接下的焊接熱影響部的低 溫韌性優異之高強度厚鋼板,進一步包含有Ca : 0.0003〜0.0050 質量 %,Mg : 0.0003〜0.0050 質量 %, REM : 0.001〜0.030質量%中的1種或2種以上,且含有 Ο ·· 0.0010〜0.0050質量%及1〇〇個/mm2以上的投影面積 直徑為0.005〜0.5//m的氧化物。 (3)如上述(1)或(2)記載之於大入熱焊接下的焊接熱影響部 的低溫韌性優異之高強度厚鋼板,進一步含有B : 8 200538561 0.0005〜0.0050質量 %。 (4)如上述(1)至(3)中任一項記載之於大入熱焊接下的焊接 熱影響部的低溫韌性優異之高強度厚鋼板,進一步含有 Cr : 0· 1 〜0.5 質量 %,M〇 : 〇 〇1 〜〇 5 質量 %,V ·· 〇 〇〇5〜〇」〇 質量%、Cu : 0.1〜1.0質量%中的1種或2種以上。 圖式簡單說明 第1圖係顯示相當於45kJ/mm的焊接熱循環之圖。Ni / Mn ^ 10xCeq-3 (0.36 &lt; Ceq &lt; 0.42) [1] 5 However, Ceq = C + Mn / 6 + (Cr + Mo + V) / 5 + (Ni + Cu) / 15, and the rest is Iron and inevitable impurities. (2) As described in (1) above, the high-strength thick steel plate having excellent low-temperature toughness in a welded heat-affected zone under large-input heat welding further contains Ca: 0.0003 to 0.0050 mass%, Mg: 0.0003 to 0.0050 mass%, REM: One or two or more of 0.001 to 0.030% by mass, and containing 0.000 to 0.0050% by mass and 100 pieces / mm2 or more of an oxide having a projected area diameter of 0.005 to 0.5 // m. (3) The high-strength thick steel plate having excellent low-temperature toughness in a welded heat-affected zone under large-entry heat welding as described in (1) or (2) above, further containing B: 8 200538561 0.0005 to 0.0050 mass%. (4) The high-strength thick steel plate excellent in low-temperature toughness in a welded heat-affected zone under large-entry heat welding as described in any one of (1) to (3) above, further containing Cr: 0. 1 to 0.5% by mass , 〇: 〇〇1〜〇5 mass%, V ·· 〇〇005〜〇 ″ 〇 mass%, Cu: 0.1 to 1.0 mass% of one or two or more. Brief Description of Drawings Figure 1 shows a welding thermal cycle equivalent to 45 kJ / mm.

10 1510 15

20 第2圖係顯示Ni/Mn、Ceq、再現HAZ韌性之關係圖。 弟3圖係顯示藉著分散微細氧化物或有效利用b使再現 HAZ韌性提高之效果之圖。 I:實施方式3 發明之較佳實施形態 以下,詳細地說明本發明。 至今用來提咼HAZ韋刃性的方法如前所述係抑制於高溫 下的沃斯田鐵晶粒的成長。其中最有效的方法係藉著分散 粒子將沃斯田鐵的晶界鎖定,阻止晶界的移動。此方法即 使於焊接入熱為20〜100kJ/mm的大入熱時,HAZ的再加熱沃 斯田鐵晶粒亦藉著鎖定可極為有效地細粒化。但是,於為 了提高母材強度使合金添加量增加且顯示鋼材的焊接性與 化學成份的淬火性之碳當量(Ceq)為〇·36以上的鋼材中,由 於HAZ的硬度變較高,故即使再加熱沃斯田鐵晶粒因鎖定 而細粒化時亦有無法得到充份地HAZ韌性之新的問題產 生。因此,於HAZ部的硬度變高時,必須使肥粒鐵的韌性 提南。 9 200538561 因此,發明者們為了改善高強度厚鋼所必要的Ceq為 〇·36以上、0·42以下高時的HAZ韌性,對用以改善肥粒鐵的 韌性之最適當成份系統進行銳意檢討。用以提高母材韌性 的元素已知Ni為有效。但是,此次對於改善Ceq為0.36以 5上、0·42以下高的HAZ韌性是否有效,又,有效時其成份 條件為何則尚未知。因此,首先檢討Ni添加量的影響。檢20 Figure 2 shows the relationship between Ni / Mn, Ceq, and reproduced HAZ toughness. Figure 3 is a graph showing the effect of improving the toughness of HAZ by dispersing fine oxides or using b effectively. I: Embodiment 3 Preferred Embodiments of the Invention The present invention will be described in detail below. The method used to improve the HAZ edge-to-edge properties so far is to suppress the growth of Vostian iron grains at high temperatures as described above. One of the most effective methods is to lock the grain boundaries of Vostian iron by dispersing the particles to prevent the grain boundaries from moving. In this method, even when the welding heat input is a large heat input of 20 to 100 kJ / mm, the reheating of the VAZDA iron grains of the HAZ can be extremely fine-grained by locking. However, in order to increase the strength of the base metal, the amount of alloy added is increased, and the carbon equivalent (Ceq) of the steel which shows weldability and hardenability of the chemical composition is 0.36 or higher, because the hardness of the HAZ becomes higher, so When the reheated Vosted iron grains are fine-grained due to locking, a new problem arises in that sufficient HAZ toughness cannot be obtained. Therefore, when the hardness of the HAZ portion becomes high, it is necessary to increase the toughness of the ferrous iron to the south. 9 200538561 Therefore, in order to improve the HAZ toughness when the Ceq required for high-strength thick steel is 0.336 or more and 0.42 or less, the inventors conducted an intensive review of the most suitable ingredient system to improve the toughness of fertilizer iron. . An element for improving the toughness of the base metal is known to be effective. However, this time it is not effective to improve the HAZ toughness with Ceq of 0.36 to 5 and 0.42 or less, and it is unknown whether the composition conditions are effective. Therefore, first, the influence of the amount of Ni added is reviewed. Check

討時,以添加0.003%以上的可有效確保母材強度的灿量為 前提。於HAZ韌性的評價上,採用給予如第1圖所示的相當 於電氣焊接(入熱45kJ/mm)的熱循環時的查拜式(Charpy)衝 10 擊試驗下的延性及脆性遷移溫度(vTrs)。 經檢討Ni添加量的影響量,首先,明白於见比〇 8%少 時無法得到必要的韌性。又,即使添加〇·8%以上的Ni,發 現亦無法改善HAZ韌性,相反地HAZ韌性下降。因此,進 一步銳意檢討包含其他的添加元素或與Ceq的關係,結果發 15現於Ceq為0·36以上、0·42以下時,如第2圖所示,HAZ韌性 與Ceq及Ni/Mn的關係。第2圖係將檢討的鋼材的再現ηΑΖ 韋刃性(vTrs)依照各Ceq分層別類,以Ni/Mn&amp;為橫軸繪出。 由第2圖可知,於Ni/Mng10xCeq_3 〔丨〕的關係成立的 鋼材中’ v Tr s為-15 °C以下可得到良好的韌性。不滿足式〔i〕 20的鋼材無法得到充份的HAZ韌性的理由為,由於Ni的添加 ΐ不足,母材的高韌化效果小,或即使含很多的Ni但因Mn 的過剩添加而於HAZ中生成厘八,使妬的高韌化效果消失所 故。進而,將上述檢討的鋼材以相當於入熱1〇〇kJ/mm的熱 循環進行相同的檢討,結果確認即使於入熱1〇〇1^111111時’ 200538561 滿足式〔1〕關係的鋼材亦得到良好的再現HAZ韋刃性。 由上述檢討發現HAZ韌性可藉著滿足式〔丨〕與添加 0.8%以上的Ni而改善,但發明者們檢討更進一步的改善 HAZ轫性。檢討以下三個改善HAZ勃性的方法。第一方法, 5由於於大入熱焊接時長期滯留於高溫,故沃斯田鐵晶粒粗 大化,此為使HAZ韌性下降的原因,因此,抑制高溫滯留 時的沃斯田鐵的粗大化。第二方法,由於大入熱焊接的焊 接後的冷卻時間很長,故由沃斯田鐵晶界生成的肥粒鐵會 粗大化,此粗大的晶界肥粒鐵成為haz韌性下降的原因, 10因此,抑制晶界肥粒鐵之粗大化。第三方法係組織 本身微細化。In this case, the premise of adding 0.003% or more can effectively ensure the strength of the base metal. For the evaluation of the HAZ toughness, the ductility and brittleness migration temperature (Charpy) at the time of a 10-stroke test at the time of applying a heat cycle equivalent to electrical welding (heating 45 kJ / mm) as shown in Fig. 1 ( vTrs). After reviewing the influence of the amount of Ni added, it is first understood that the necessary toughness cannot be obtained when it is less than 0.8%. In addition, even when Ni was added in an amount of 0.8% or more, it was found that the HAZ toughness could not be improved, and conversely, the HAZ toughness decreased. Therefore, further intensive review included other added elements or the relationship with Ceq, and the results were found to be 15 when Ceq is 0.36 or more and 0.42 or less. As shown in Figure 2, HAZ toughness is related to Ceq and Ni / Mn. relationship. Fig. 2 is a plot of the reproduced steel material ηΔZ (VTrs) of the steel under review in accordance with the respective Ceq layering types, with Ni / Mn &amp; as the horizontal axis. From Fig. 2, it can be seen that good toughness can be obtained in a steel material where 'v Tr s is -15 ° C or less in the Ni / Mng10xCeq_3 [丨] relationship. The reason why the steel that does not satisfy the formula [i] 20 cannot obtain sufficient HAZ toughness is because the addition of Ni is insufficient, and the high toughness effect of the base material is small, or even if it contains a large amount of Ni, it is caused by excessive addition of Mn. HAZ is formed in Haze, which makes the high toughness effect of jealousy disappear. Furthermore, the steel materials reviewed above were subjected to the same review with a thermal cycle corresponding to a heat input of 100 kJ / mm. As a result, it was confirmed that the steel materials satisfying the relationship of formula [1] even when the heat input was 1001 ^ 111111. Get good reproducibility of HAZ. From the above review, it was found that the HAZ toughness can be improved by satisfying the formula [丨] and adding more than 0.8% Ni, but the inventors reviewed to further improve the HAZ resistance. Review the following three ways to improve the HAZ viability. In the first method, 5 due to the long-term retention at high temperature during large-entry heat welding, the grain size of Vosstian iron is coarsened. This is the cause of the decrease in HAZ toughness. Therefore, the coarsening of Vosstian iron during high-temperature retention is suppressed. In the second method, since the cooling time after the large-scale thermal welding is very long, the ferrous grain iron produced by the Vostian iron grain boundary will coarsen. This coarse grain boundary ferrous grain iron will cause the haz toughness to decrease. 10 Therefore , To suppress the coarsening of grain boundary fertilizer grain iron. The third method is to miniaturize the organization itself.

關於第一個抑制沃斯田鐵晶粒的粗大化的方法,例如 於專利文獻7所記載的使微細氧化物分散的方法為有效。於 專利文獻7中,於微細氧化物的分散上係於脫氧步驟中將溶 15鋼的溶存氧量以與Si的平衡反應加以調整,進而之後以Ti、 A卜Ca的順序脫氧。依該方法,將粒徑為〇·〇1〜1〇//ιη的氧 化物以5x103〜1x1 〇5個/mm2分散。 因此,發明者們銳意檢討Ceq為0.36以上、〇·42以下高 時’於包含0.003%的Nb且添加0.8%以上的Ni的系統中,使 20 微細氧化物分散,進一步提高HAZ韌性之方法。首先發現 一種使微細氧化物分散之方法,該方法係於該系統中,於 脫氧步驟中將溶鋼的溶存氧量調整至0.0010〜0.0050%後, 首先以Ti脫氧,接著以A1脫氧後,進一步藉著添加Ca、Mg、 REM中的1種以上,可使投影面積直徑為〇·〇〇5〜〇.5//m的微 11 200538561 細氧化物以100個/mm2以上分散。又,藉著此微細氧化物的 分散,可抑制焊接時的高溫滯留時的沃斯田鐵晶粒粗大 化,可進一步改善HAZ韌性。與僅適當添加Ni的HAZ韌性 相比較的結果之一例顯示於第3圖。進而,生成的氧化物其 5 Ni的量愈多愈細,個數愈多,Ni量為1.5%以上時成為1000 個/mm2以上。此為本次發現之事。進一步,關於溶鋼中的Regarding the first method for suppressing the coarsening of the Vosted iron grains, for example, the method of dispersing fine oxides described in Patent Document 7 is effective. In Patent Document 7, the dispersion of fine oxides is performed in a deoxidation step to adjust the amount of dissolved oxygen in the dissolved steel in a balanced reaction with Si, and then deoxidizes in the order of Ti and Ab. According to this method, oxides having a particle size of 0.001 to 10 // ιη are dispersed at 5x103 to 1x105 particles / mm2. Therefore, the inventors have eagerly reviewed a method for dispersing 20 fine oxides in a system containing 0.003% Nb and adding 0.8% or more Ni when the Ceq is 0.36 or more and 0.42 or less, to further improve the HAZ toughness. Firstly, a method for dispersing fine oxide was found. This method is based on the system. In the deoxidation step, the dissolved oxygen content of the dissolved steel is adjusted to 0.0010 ~ 0.0050%, and then first deoxidized with Ti, then deoxidized with A1, and further borrowed. By adding one or more of Ca, Mg, and REM, it is possible to disperse micro 11 200538561 fine oxides having a projection area diameter of 0.05 to 0.5 // m at 100 particles / mm2 or more. Further, by dispersing this fine oxide, coarsening of the Vosted iron grains during high-temperature retention during welding can be suppressed, and the HAZ toughness can be further improved. An example of the results compared with the HAZ toughness with the proper addition of Ni is shown in Fig. 3. Furthermore, the more the amount of 5 Ni formed, the finer the number of oxides, and the larger the number of oxides. When the amount of Ni is 1.5% or more, it becomes 1,000 pieces / mm2 or more. This is the discovery. Further, about the

Si量,由於Si量多時氧化物變得很難生成,故由本次檢討中 可知Si量為0.30%以下、進而為〇·2〇%以下為佳。另一方面, Ti脫氧前的溶存氧量超過0.0050%時或脫氧元素的順序不 10同時,由於氧化物會粗大化,無法充份地得到微細氧化物, 故幾乎沒有抑制沃斯田鐵晶粒的粗大化的效果。又,投影 面積直徑為0.005〜0.5 // m的氧化物的個數係藉著由母材之 鋼板製作抽提複製品,將其以電子顯微鏡以1〇〇〇〇倍觀察 1〇〇視野以上(觀察面積為1〇〇〇〇//m2以上),關於未滿〇3从 15 m的粒子則提高適當倍率觀察。對觀察的0.005〜0.5//m直徑 的各粒子進行元素分析,計算氧化物的數量。 接著,發明者們銳意檢討上述的第二及第三個使haz 韌性提高的方法,即抑制晶界肥粒鐵的粗大化及使HAZ組 哉d田化。結果發現,於Ceq為0.36以上、〇·42以下高時且 20添加0.8%以上的Ni的系、、統中,特別是進行本次的相當於 =〜1000kJ/mm的大入熱焊接時,添加B為有效。其理由為, 從抑制晶界肥粒鐵粗大化的點來看,藉著固溶B於加熱沃斯 载曰曰界偏析可抑制晶界肥粒鐵的生成。又,從HAZ組織 的細微化的點來看,於本次的大人熱焊接中冷卻速度慢 12 200538561 5 10The amount of Si is difficult to form oxides when the amount of Si is large. From this review, it is found that the amount of Si is preferably 0.30% or less, and more preferably 0.20% or less. On the other hand, when the amount of dissolved oxygen before Ti deoxidation exceeds 0.0050% or the order of the deoxidizing elements is not 10, the oxides will coarsen and fine oxides cannot be obtained sufficiently, so the coarsening of the grains of Vostian iron is hardly suppressed The effect. In addition, the number of oxides having a projection area diameter of 0.005 to 0.5 // m is obtained by making an extraction replica from a steel plate of a base material, and observing it with an electron microscope at a magnification of 10,000 times and a field of view of 1,000 or more. (Observation area is 10000 // m2 or more.) For particles less than 15 m from 15 m, the observation rate is increased at an appropriate magnification. Elemental analysis was performed on each particle having a diameter of 0.005 to 0.5 // m observed, and the number of oxides was calculated. Next, the inventors made an intensive review of the second and third methods to improve the haz toughness, that is, to suppress the coarsening of the iron grains in the grain boundary and to make the HAZ group 田 d field. As a result, it was found that when the Ceq is 0.36 or more and 0.42 or less, and 0.8% or more of Ni is added to the system, especially when the large-entry heat welding equivalent to = ~ 1000kJ / mm is performed this time, Adding B is effective. The reason is that, from the point of suppressing coarsening of grain-boundary grain iron, the formation of grain-boundary grain iron can be suppressed by solid solution B in heated Voss load boundary segregation. From the point of miniaturization of the HAZ structure, the cooling rate is slower in this adult thermal welding 12 200538561 5 10

時’错著添加B可於沃斯田鐵晶界及沃斯田鐵晶粒⑽内含 斤出氮化物’於沃斯田鐵晶界及晶粒内生成複數的以B 氮化物為核的數㈣的微細肥粒鐵,因此,使H A z組織微細 化。藉著添加B改善HAZ勒性與僅適當添加n_az拿刀性之 比車=、·。果颁不於第3圖。可明白藉著添加靴似緣性進一 ,提高。進而,於第3圖中雖然除了上述的使微細氧化物分 散的方法外,亦顯示添加8時的HAZ她,但藉著分散微細 氧化物與添加B可更-步使HAZ韋刃性提高。其原因為,藉著 成為BN的析出位置的氧化物增加,以該^^^^為核的肥粒鐵增 加,HAZ組織更微細化。 又,從確保強度與提高腐食性的觀點來看,除了上述 條件外,亦檢討添加CU、Cr、Mo、V時的HAZ韌性。其結 果發現右分別添加〇.1〜0.4%、〇.1〜〇 5%、〇 〇1〜〇 2%、 0.005〜0.050%的範圍,HAZ韌性不會大幅下降。 進而,本發明之鋼板之製造方法並不特別限制,可依 照周知的方法製造。例如,可將經調整至上述適當成份組 成的溶鋼以連續鑄造法壓成厚板後,加熱至1000〜1250°c, 施予熱間壓延。 以下,說明關於限定本發明所使用的鋼材料的成份組 20 成之理由。以下,組成的質量%單純地以%表示。 C為有效提高鋼強度的成份,下限為0.03%,添加過多 時由於會大量地生成碳化物及MA,使HAZ韌性明顯地下 降,故上限為0.14%。When 'wrongly adding B, nitrides can be contained in Vostian iron grain boundaries and grains of Vostian iron grains', a plurality of micro fertilizer particles with B nitride as the core are formed in the Vostian iron grain boundaries and grains Iron therefore miniaturizes the HA z structure. The ratio of improving the HAZ legibility by adding B to n_az is only appropriate. =, ·. The result is not in Figure 3. It can be understood that by adding boots like fate further, improve. Furthermore, in Fig. 3, in addition to the method for dispersing fine oxides as described above, it is also shown that HAZ at 8 is added, but by dispersing fine oxides and adding B, the sharpness of HAZ can be further improved. The reason for this is that the HAZ structure becomes finer by increasing the amount of oxides that become the deposition sites of BN and increasing the iron content of the fertilized grains with the ^^^^ as the core. From the viewpoints of securing strength and improving rottenness, in addition to the above conditions, the HAZ toughness when CU, Cr, Mo, and V were added was also reviewed. As a result, it was found that when the ranges of 0.1 to 0.4%, 0.1 to 5%, 0.001 to 0.2%, and 0.005 to 0.050% were added to the right, the HAZ toughness did not decrease significantly. Furthermore, the method for producing the steel sheet of the present invention is not particularly limited, and it can be produced by a known method. For example, the molten steel adjusted to the above-mentioned appropriate composition can be pressed into a thick plate by a continuous casting method, then heated to 1000 to 1250 ° C, and subjected to hot rolling. The reason for limiting the component composition of the steel material used in the present invention will be described below. Hereinafter, the mass% of the composition is simply expressed as%. C is a component that effectively increases the strength of steel. The lower limit is 0.03%. When it is added too much, carbides and MA are formed in large quantities, which significantly reduces the HAZ toughness. Therefore, the upper limit is 0.14%.

Si為確保母材強度、脫氧等的必要成份,但為了防止 13 200538561 因HAZ硬化而使韌性下降,上限為0·30%。進而,為了防止 於利用氧化物時溶鋼中的氧濃度減少,故上限以0.20以下 為佳。 Μη為有效確保母材強度、韌性的成份,必須添加0.8% 以上’但於焊接部的韌性、破裂性等可容許的範圍内,上 限為2·0%。進一步,關於Μη的上限,必須滿足顯示Ceq、Si is an essential component to ensure the strength of the base metal and deoxidation, but in order to prevent the decrease in toughness due to HAZ hardening, the upper limit is 0.30%. Furthermore, in order to prevent a decrease in the oxygen concentration in the dissolved steel when using an oxide, the upper limit is preferably 0.20 or less. Mn is a component that effectively ensures the strength and toughness of the base metal, and must be added at 0.8% or more. 'However, the upper limit is 2.0% within the allowable range of the toughness and fracture properties of the welded portion. Further, regarding the upper limit of Μη, the display Ceq,

Mn量及Ni量的關係之式〔1〕。此為本次檢討中的新的發 現。基於Ceq過高時Μη的增加為使MA大量生成於HAZ組織 的原因’而使Ni所帶來的ΗΑΖ韌性的提高效果消失。 10 \The relationship [1] between the amount of Mn and the amount of Ni. This is a new finding in this review. The increase in Mη when Ceq is too high is the reason that a large amount of MA is generated in the HAZ structure, and the effect of improving the toughness of ΗΑZ due to Ni disappears. 10 \

Ni/Mn^l〇xCeq-3 [ 1) P的含有量愈少愈好,但由於工業上的使其含有量減低 會增加很多成本,故含有範圍為0.02以下。 S的含有量愈少愈好,但由於工業上的使其含有量減低 會增加很多成本,故含有範圍為0.005以下。 15Ni / Mn ^ 10xCeq-3 [1] The smaller the content of P, the better. However, reducing it in industry will increase a lot of cost, so the content range is 0.02 or less. The smaller the content of S, the better. However, industrially reducing the content of S will increase a lot of costs, so the content range is 0.005 or less. 15

Ni為本發明中重要的元素,至少必須添加〇 8%以上。 進而’關於Ni的下限’必須滿足顯示Ceq、Μη量及Ni量的 關係之式〔1〕。關於上限,從製邊成本的觀點來看,為4 〇%。 Ni/Mn^lOxCeq-3〔1〕Ni is an important element in the present invention, and at least 0.8% must be added. Furthermore, "about the lower limit of Ni" must satisfy the formula [1] showing the relationship between the Ceq, the amount of Mη, and the amount of Ni. The upper limit is 40% from the viewpoint of the cost of edge making. Ni / Mn ^ lOxCeq-3 [1]

Nb為用以提高淬火性而有效地使母材強度提高的元 2〇 寺 '、 添加0.003%以上。但是,添加過多Nb時,與Ni/Mn比 無關’於HAZ中變得容易生成MA,添加0.040%以上時,於 HAZ中會生成複數的長徑5以01以上的粗大的MA,使HAZ 初性大幅下降,因此,Nb的上限為0.040%。又,為了得到 最向的韌性,於滿足上述式〔1〕的Ni/Mn比下,宜將Nb量 14 200538561 抑制於各乎不會生成長徑5 // m以上的粗大MA的〇 〇2〇%以 下。為了更安定地得到更進-步高_性,於滿足上述式 〔1〕的价論比下,宜將Nb量抑制於幾乎不會生成長徑3 //m以上的MA的〇·〇ι〇%以下。 A1為重要的脫氧元素’下限值為0.001%。X,A1大量 存在時,由於鑄片的表面品f會劣化,故上限為讀〇%。Nb is used to improve the hardenability and effectively increase the strength of the base metal. Add 0.003% or more. However, when too much Nb is added, it has nothing to do with the Ni / Mn ratio. MA becomes easy to generate in HAZ. When 0.040% or more is added, coarse MA with a complex major diameter of 5 or more is generated in HAZ. Since the performance is greatly reduced, the upper limit of Nb is 0.040%. In addition, in order to obtain the toughest toughness, the Nb content 14 200538561 should be suppressed to 0,02 which does not generate a coarse MA with a long diameter of 5 // m or more under the Ni / Mn ratio satisfying the above formula [1]. 〇% or less. In order to obtain a more stable step-height property, under the valence ratio that satisfies the above formula [1], it is appropriate to suppress the amount of Nb to 0 · 〇ι that hardly generates MA with a long diameter of 3 // m or more. 〇% or less. The lower limit of A1 as an important deoxidizing element is 0.001%. When X and A1 are present in a large amount, the surface quality f of the slab deteriorates, so the upper limit is 0%.

Ti係用以生成於抑制再加熱沃斯田鐵晶粒的粗大化上 所必須的鎖絲子之Ti氮化物及含有ή氧化物,添加 0.005%以上。但是, 多餘的添加由於會使固溶Ti量增加, 10招來HAZ韌性下降,故以〇〇3〇%為上限。 N係用以於焊接後的冷卻中於沃斯田鐵晶界及晶粒内 生成Ti氮化物及B氮化物,可視需要調整其添加量。為了與 B相結合形成B氮化物’必須添加_腾以上,但多餘的 添加由於會使固溶N量增加,招來HAZ韋刃性下降,故以 15 0.0100%為上限。Ti is used to generate Ti nitrides and oxides containing lock wires that are necessary for suppressing the coarsening of the reheated Vosted iron grains. Add 0.005% or more. However, the excessive addition will increase the amount of solid solution Ti and decrease the HAZ toughness. Therefore, the upper limit is 0.30%. N is used to form Ti nitrides and B nitrides in the grain boundaries and grains of Vostian iron during cooling after welding, and the addition amount can be adjusted as required. In order to combine with B to form B-nitride ', it is necessary to add more than tenths. However, the excess addition will increase the amount of solid solution N, which will cause the HAZ cutting edge to decrease, so the upper limit is 15 0.0100%.

Ca係用以生成於抑制再加缺斯明晶粒的粗大化上 所必須的鎖定粒子之叫氧化物,可視需要添加0._3% 以上。但是,多餘的添加由於會生成粗大的内含物,故以 0.0050%為上限。 20 岣係用以生成於抑制再加熱沃斯田鐵晶粒的粗大化 上所必須的鎖定,子之%系氧化物,可視需要添加 物,故以謂爾上限 由於會生成粗大的内含 REM係用以生成於抑制再加熱沃斯田鐵晶粒的粗大化 15 200538561 上所必須的鎖定粒子之REM系氧化物,可視需要添加 0.001%以上。但是,多餘的添加由於會生成粗大的内含物, 故以〇·〇3〇%為上限。又,於此所謂的REM係Ce及La,添加 量為兩者的總量。 6係用以作為固溶B,於焊接後的冷卻中偏析於沃斯田 鐵晶界’抑制晶界肥粒鐵的生成,又,為了使BN生成於沃 斯田鐵晶界或晶粒内,可視需要添加0.0005%以上。但是, 多餘的添加由於會使固溶B量增大,使HAZ硬度大幅上昇, 招來HAZ韌性下降,故以0.0050%為上限。Ca is an oxide that is used to generate locked particles that are necessary to suppress the coarsening of the additional Smell grains, and can be added at a level of more than 0. _3% as needed. However, excessive addition will cause coarse inclusions, so the upper limit is 0.0050%. 20 Samarium is used to generate the necessary lock to suppress the reheating of the grains of reheated Vosted iron. The %% oxide is an additive that can be added if necessary. Therefore, the upper limit of the sol is to produce a coarse inclusion of REM. In order to suppress the coarsening of the reheated Vosted iron grains 15 200538561, it is necessary to add REM-based oxides to the REM-based oxides, which can be added by more than 0.001% as needed. However, since the excessive addition generates coarse inclusions, the upper limit is set to 0.030%. The REM-based Ce and La are referred to herein as the total amount of both. The 6 series is used as solid solution B, which is segregated at the Vostian iron grain boundary during cooling after welding to suppress the formation of grain boundary ferrous iron. In addition, in order to generate BN in the Vostian iron grain boundary or grain, it may be added as needed. Above 0.0005%. However, the excessive addition will increase the amount of solid solution B, greatly increase the HAZ hardness, and invite a decrease in HAZ toughness. Therefore, the upper limit is 0.0050%.

Cu係用以使鋼材的強度及耐腐性提高,可視需要添加 0.1%以上。其效果由於於1.0%飽和,故上限為1.0%,但由 於超過0.4%時易生成MA,使HAZ韌性下降,故以〇·4%以下 為較佳。Cu is used to improve the strength and corrosion resistance of steel, and it can be added above 0.1% if necessary. The effect is saturated at 1.0%, so the upper limit is 1.0%. However, since MA is easily generated when the content exceeds 0.4%, and the HAZ toughness is reduced, it is preferably 0.4% or less.

Cr係用以使鋼材的耐腐性提高,可視需要添加〇1%以Cr is used to improve the corrosion resistance of steel.

15上,但多餘的添加由於會因MA的生成招來HAZ韌性的下 降,故以0.5%為上限。15%, but the excessive addition will reduce the HAZ toughness due to the formation of MA, so the upper limit is 0.5%.

Mo係用以使母材的強度及耐腐性有效地提高的元 素,可視需要添加0.01%以上。其效果由於於〇 5%飽和,故 上限為0.5% ’但由於多餘的添加會因μα的生成招來HAZ 20 勃性的下降,故以0.2%以下為較佳。 V係用以使母材的強度有效地提高的元素,可視需要 添加0.005%以上。其效果由於於〇1〇%飽和,故上限為 0.10%,但由於多餘的添加會aMA的生成招來ΗΑΖ韌性的 下降,故以0.050%以下為較佳。 16 200538561 實施例1Mo is an element used to effectively improve the strength and corrosion resistance of the base material, and may be added by 0.01% or more as necessary. The effect is saturated at 0.5%, so the upper limit is 0.5% '. However, since the addition of extra α causes a decrease in HAZ 20's vigor due to the formation of μα, it is preferably 0.2% or less. V is an element used to effectively increase the strength of the base material. If necessary, 0.005% or more is added. The effect is saturated at 010%, so the upper limit is 0.10%. However, since the addition of aMA will cause a decrease in the toughness of ΗΑZ, it is preferably 0.050% or less. 16 200538561 Example 1

連續鑄造表1所示化學成份的溶鋼,製作鋼片。關於 D23〜D34、D46〜D49,於投入Ti之前將溶鋼的溶存氧以si 調整至0.0010%〜0.0050%,之後,首先以Ti脫氧,接著以A1 5 脫氧後,添加Ca、Mg、REM中的任一者,進行脫氧。將該 等於1100〜1250°C下再加熱後,以以下2種壓延方法製造板 厚50〜80mm的鋼板。一種為於表面溫度750〜900。(:的溫度範 圍下壓延後,水冷至復熱後的板表面溫度成為2〇〇〜4〇〇°C的 溫度範圍之方法(於表2記為TMCP),另一種為熱軋壓延後 10 水冷至室溫,於500〜600°C的範圍下進行回火之製造方法 (於表2記為DQ-T)。 於表2顯示鋼板的製造條件、板厚、機械性質。又,關 於D23〜D34、D46〜D49,一併記载有經測定鋼板的任意處 之投影面積直徑為0.005〜0.5//m的微細氧化物的個數。氧 15化物的個數係藉著由鋼板的任意處製作抽提複製品,將其 於電子顯微鏡以10000倍觀察100視野以上(觀察面積為 10000 // m2以上)’關於未滿0· 1 // m的粒子則提高適當倍率 觀察。對觀察的0.005〜0.5//m直經的各粒子進行元素分 析’計算氧化物的數量。D23〜D31、j)46〜D49的鋼材中皆 20分散有本發明範圍之1⑻個/mm2的投影面積直徑為〇 01〜〇·5 //m的微細氧化物。進而,對Si以外的元素幾乎都相同的 D46、D47及D48、D49進行比較,可明白^量為〇 20%以下 時氧化物的量愈多。 對該等鋼板使用焊接入熱量為2〇〜i〇〇kJ/mm的電氣焊 17 200538561 接(EGW)或電熔渣焊接(ESW),將鋼板對接,立起相對地進 行1回焊接。然後,於位於板厚中央部(t/2)的haz中,於距 離FLlmm的HAZ與FL二處放入刻痕,於-4(rc進行查拜式衝 擊試驗。於表2顯示焊接條件及HAZ韌性。於此,於查拜式 5衝擊試驗中’使用JIS4號的2mmV刻痕的全尺寸試驗片。 又,於表2中,一併記入FL〜HAZlmm間的舊沃斯田鐵粒徑。 於此記載的FL〜HAZlmm間的舊沃斯田鐵粒徑係將被包含 於含有以板厚中央部為中心的板厚方向2mm與 FL〜HAZlmm的面的舊沃斯田鐵晶粒的粒徑以截面法測定 10的平均粒徑。進而,於此,將連結成網狀的塊狀肥粒鐵作 為舊沃斯田鐵晶粒的晶界進行測定。 15The molten steel with the chemical composition shown in Table 1 was continuously cast to produce a steel sheet. Regarding D23 to D34 and D46 to D49, the dissolved oxygen of dissolved steel was adjusted to 0.0010% to 0.0050% by si before Ti was introduced, and then deoxidation with Ti was followed by deoxidation with A1 5 and Ca, Mg, and REM were added. In either case, deoxidation is performed. After reheating at a temperature of 1100 to 1250 ° C, a steel sheet having a thickness of 50 to 80 mm is manufactured by the following two rolling methods. One is at a surface temperature of 750 ~ 900. (After rolling under the temperature range, the method of cooling the plate surface temperature after water reheating to a temperature range of 2000 ~ 400 ° C (referred to as TMCP in Table 2), the other is 10 after hot rolling and rolling Water-cooled to room temperature, and a tempering method in the range of 500 to 600 ° C (referred to as DQ-T in Table 2). Table 2 shows the steel plate manufacturing conditions, plate thickness, and mechanical properties. Also, D23 ~ D34, D46 ~ D49, the number of fine oxides with a projected area diameter of 0.005 ~ 0.5 // m measured at any place on the steel sheet is also recorded. The number of oxygen 15 compounds is determined by any place on the steel sheet. Make an extraction replica and observe it under an electron microscope at a magnification of 10,000 times and a field of view of 100 or more (observation area is 10000 // m2 or more). For particles less than 0 · 1 // m, increase the observation at an appropriate magnification. 0.005 for observation Elementary analysis of each particle with a diameter of ~ 0.5 / m 'is used to calculate the number of oxides. D23 to D31, j) 46 to D49 are all 20 steel dispersed with a projected area of 1 发明 / mm2 in the scope of the invention. The diameter of the projected area is 0. 01 ~ 〇 · 5 // m fine oxide. Furthermore, when D46, D47, D48, and D49, which have almost the same elements other than Si, are compared, it can be understood that the larger the amount of oxide is, the greater the amount of oxide is. These steel plates are welded by electric welding with a heat input of 20 to 100 kJ / mm. 17 200538561 (EGW) or electric slag welding (ESW), butt the steel plates and perform one-time welding. Then, in the haz located at the center of the plate thickness (t / 2), place a score at two locations HAZ and FL from FLlmm, and perform a Chapel impact test at -4 (rc. Table 2 shows the welding conditions and HAZ toughness. Here, in the Charpy 5 impact test, a full-size test piece using 2mmV nicks of JIS No. 4 was used. In Table 2, the particle size of old Vostian iron between FL and HAZlmm was also recorded. The particle size of the old Vosstian iron grains between FL and HAZlmm described here is included in the grain size of the old Vosstian iron grains including the plane thickness direction 2mm centered on the plate thickness center and the FL to HAZlmm plane The average particle diameter of 10 was measured by a cross-section method. Further, here, the bulk ferrous iron connected in a network shape was measured as a grain boundary of old Vosted iron grains. 15

D1〜D49為本發明鋼。由於鋼的化學成份被適當地控 制’故滿足預定的母材性能,且於_40°C的大入熱HAZ韌性 良好。又,經使微細氧化物分散的D23〜D34、D46〜D49, 其FL〜HAZlmm間的舊沃斯田鐵粒徑成為200//m以下,比 其他細的晶粒,於-40°C下的大入熱HAZ韌性亦進一步提 南。又’經添加B謀求HAZ組織的微細化的D20與未添加B 但B以外的添加元素相同的〇19相比較,D20的HAZ韌性良 好,於-40°C下的大入熱HAZ韌性亦顯示高的值。 20 另一方面,比較鋼C1〜17由於不含滿足式〔1〕的充份 的Ni或鋼的化學成份沒有被適當地控制,故大入熱HAZ韌 性不足。 18 200538561 表1D1 to D49 are steels of the present invention. Since the chemical composition of the steel is appropriately controlled ', it satisfies the predetermined properties of the base metal, and has a high HAZ toughness at -40 ° C. In addition, after D23 to D34 and D46 to D49 in which fine oxides are dispersed, the old Vosted iron particle size between FL and HAZlmm becomes 200 // m or less, which is lower than other fine grains at -40 ° C. The large-entry heat HAZ toughness is also further raised. In addition, compared with D19, where the addition of B is used to refine the HAZ structure, compared with 〇19, which does not contain B but has the same addition elements as B, D20 has a good HAZ toughness, and the HAZ toughness at -40 ° C is also shown. High value. 20 On the other hand, Comparative Steels C1 to 17 do not contain sufficient Ni or the chemical composition of the steel which satisfies the formula [1], and the chemical composition of the steel is not properly controlled, so the toughness of the HAZ is insufficient. 18 200538561 Table 1

區分 記號 C Si Μη Ρ S Νί Nb A) Ti N Ca Mg 發明銅 D1 0.04 0.13 1.31 0.008 0.002 1.6 0.006 0.015 0.008 0.0035 02 0.04 0.17 0.81 0.008 0.002 2.8 0.006 0Ό15 0008 0.0035 D3 0Ό7 0.17 1.40 αο〇7 0.002 0.9 0.006 0.015 0.007 0.0035 D4 0.07 0.05 0.81 0Ό06 0.002 2.4 0.006 0.014 0.008 0.0035 D5 0.10 0.19 1.11 0.007 0.002 1.1 0.004 0.015 0.007 0.0032 D6 0.13 0.05 0.91 0.007 0.003 1.2 ; 0.005 丨 0.014 0.006 0.0037 D7 0.06 0.19 1.41 0.007 0.002 1.3 0.005 0.012 0.006 0.0042 D8 0.06 0.22 1,11 0.006 0.003 2.1 0.005 0.014 0.006 0.0035 D9 0.0S 0.15 1.21 0.007 0.003 1.4 0.006 0.015 0.006 0.0035 D10 0.12 0.11 1.01 0.007 αο〇2 1.4 0.005 0.014 0Ό09 0.0035 D11 0.13 0.14 0.91 0.006 0.002 1.5 0.006 0.015 0.008 0.0035 D12 0.06 0.14 1.41 0.007 0.002 1.6 0.005 0.014 0.008 0.0032 D13 0.06 0.22 1.11 0.007 0.002 2.4 0.005 0.014 0Ό07 0.0035 D14 0.09 0.21 1.31 0.008 0.002 1.4 ; 0.005 0.014 0.0G8 0.0035 D15 0.13 0.19 1.01 0.007 0.002 1.6 0.005 0.014 0.007 0.0035 D16 0.12 0.22 0.91 0.007 0.003 2.1 0.006 0.015 0.006 0.0035 D17 0.13 0.17 1.01 0.006 0.002 1.7 0.005 0.014 0.006 0.0032 D18 0.12 0.15 1.11 0.008 0.002 1.5 0.005 0.014 0.006 0.0037 D19 0.06 0J4 1.41 0.007 0.002 1.6 0.005 0.014 0.009 0.0041 020 0.06 0.14 1.40 0.007 0.002 1.6 0.005 0.014 0Ό09 0.0041 D21 0.06 0.10 1.21 0,007 0.002 1.7 0.006 0.015 0.010 0.0035 D22 0.06 0.22 1.11 0.007 0.002 1.8 0.005 0.014 0.008 0.0055 D23 0.06 0.16 1.31 0.008 0.004 1.8 0.005 0.014 0.008 0.0035 0.0018 D24 0.06 0.17 1.40 0.008 0Ό04 1.6 0Ό05 0.014 0.008 0.0037 0.0019 D25 0.06 0.12 1.20 0.007 0.002 2.1 0.006 0.0Ϊ5 0.007 0.0033 0.0016 D26 0.06 0.15 1.00 0.007 0.002 2.6 0.005 0.014 0.008 0.0036 D27 0.06 0.11 1.21 0.007 0.002 1.8 0.015 0.015 0.007 0.0035 0.0014 D28 0.06 0.23 1.00 0Ό07 0.002 1.9 0.005 0:014 0.006 0.0035 0.0018 D29 0.06 0.17 1,20 0.008 0.004 1.8 0.005 0.014 0.006 0.0035 0.0036 D30 0Ό6 0.12 1.20 0.007 0.002 1.7 0.006 0.015 0.006 0.0035 0.0009 D31 0.06 0.12 1.20 0.007 0.002 1.9 0.006 0.015 0.006 0.0035 0.0016 D32 0.07 0.15 1.21 0.007 0.G03 1.4 0.028 0.014 0.009 0.0032 0.0015 D33 0.08 0.13 1.21 0.009 0.002 1.3 0.013 0.014 0.010 0.0052 0.0017 D34 0.08 0.19 1.21 0.008 0.003 1.5 0.013 0.025 0.008 0.0076 0.0012 D35 0.08 0.19 1.21 0.010 0.002 1.2 0.021 0.014 0.008 0.0035Distinguishing mark C Si Μη Ρ S Νί Nb A) Ti N Ca Mg Invention copper D1 0.04 0.13 1.31 0.008 0.002 1.6 0.006 0.015 0.008 0.0035 02 0.04 0.17 0.81 0.008 0.002 2.8 0.006 0Ό15 0008 0.0035 D3 037 0.17 1.40 αο〇7 0.002 0.9 0.006 0.015 0.007 0.0035 D4 0.07 0.05 0.81 0Ό06 0.002 2.4 0.006 0.014 0.008 0.0035 D5 0.10 0.19 1.11 0.007 0.002 1.1 0.004 0.015 0.007 0.0032 D6 0.13 0.05 0.91 0.007 0.003 1.2; 0.005 丨 0.014 0.006 0.0037 D7 0.06 0.19 1.41 0.007 0.002 1.3 0.005 0.012 0.006 0.0042 D8 0.06 0.22 1,11 0.006 0.003 2.1 0.005 0.014 0.006 0.0035 D9 0.0S 0.15 1.21 0.007 0.003 1.4 0.006 0.015 0.006 0.0035 D10 0.12 0.11 1.01 0.007 αο〇2 1.4 0.005 0.014 0Ό09 0.0035 D11 0.13 0.14 0.91 0.006 0.002 1.5 0.006 0.015 0.008 0.0035 D12 0.06 0.14 1.41 0.007 0.002 1.6 0.005 0.014 0.008 0.0032 D13 0.06 0.22 1.11 0.007 0.002 2.4 0.005 0.014 0Ό07 0.0035 D14 0.09 0.21 1.31 0.008 0.002 1.4; 0.005 0.014 0.0G8 0.0035 D15 0.13 0.19 1.01 0.007 0.002 1.6 0.005 0.014 0.0 07 0.0035 D16 0.12 0.22 0.91 0.007 0.003 2.1 0.006 0.015 0.006 0.0035 D17 0.13 0.17 1.01 0.006 0.002 1.7 0.005 0.014 0.006 0.0032 D18 0.12 0.15 1.11 0.008 0.002 1.5 0.005 0.014 0.006 0.0037 D19 0.06 0J4 1.41 0.007 0.002 1.6 0.005 0.014 0.00 0.0041 020 0.06 0.14 1.40 0.007 0.002 1.6 0.005 0.014 0Ό09 0.0041 D21 0.06 0.10 1.21 0,007 0.002 1.7 0.006 0.015 0.010 0.0035 D22 0.06 0.22 1.11 0.007 0.002 1.8 0.005 0.014 0.008 0.0055 D23 0.06 0.16 1.31 0.008 0.004 1.8 0.005 0.014 0.008 0.0035 0.0018 D24 0.06 0.17 1.40 0.008 0 04 0.008 0.0037 0.0019 D25 0.06 0.12 1.20 0.007 0.002 2.1 0.006 0.0Ϊ5 0.007 0.0033 0.0016 D26 0.06 0.15 1.00 0.007 0.002 2.6 0.005 0.014 0.008 0.0036 D27 0.06 0.11 1.21 0.007 0.002 1.8 0.015 0.015 0.007 0.0035 0.0014 0.002 D28 0.06 0.23 1.00 0Ό07 0.002 1.9 0.005 0: 014 0.006 0.0035 0.0018 D29 0.06 0.17 1,20 0.008 0.004 1.8 0.005 0.014 0.006 0.0035 0.0036 D30 0Ό6 0.12 1.20 0.007 0.002 1.7 0.006 0.015 0.006 0.0035 0.0009 D31 0.06 0.12 1.20 0.007 0.002 1.9 0.006 0.015 0.006 0.0035 0.0016 D32 0.07 0.15 1.21 0.007 0.G03 1.4 0.028 0.014 0.009 0.0032 0.0015 D33 0.08 0.13 1.21 0.00 0.002 1.3 0.013 0.014 0.010 0.0052 0.0017 D34 0.08 0.19 1.21 0.008 0.003 1.5 0.013 0.025 0.008 0.0076 0.0012 0.0012 D35 0.08 0.19 1.21 0.010 0.002 1.2 0.021 0.014 0.008 0.0035

19 200538561 表1之119 200538561 Table 1 of 1

區分 REM 〇 8 Cu Cr Mo V Ceq Ni/Mn 10 x Ceq -3 判定* 0.37 1.22 0.7 〇 0.36 3.46 0.6 〇 0.36 0.64 0.6 〇 0.37 2.96 0.7 〇 0.36 0.99 0.6 〇 0.36 1.32 0.6 〇 0.38 0.92 0.8 〇 0.39 1.89 0.9 〇 0.39 1.16 0.9 〇 0.38 1.39 : 0.8 〇 0,38 1.65 0.8 〇 0.40 1.13 1.0 〇 0.41 2.16 1.1 〇 0.40 1.07 1.0 〇 0.41 1.58 1.1 Ο 0.41 2.31 1.1 〇 發明鋼 0.41 1.68 1.1 〇 0.41 1.35 1.1 〇 0.40 1.13 1.0 〇 0.0012 0.40 1.14 1.0 〇 0.4 ΟΛΟ 1.40 1.0 〇 0.0023 0.2 0.41 1.62 1.1 〇 0.0019 0.40 1.37 1.0 〇 0.0019 0.0008 0.40 1.14 1.0 〇 0.0017 0.0009 0.40 1.75 1.0 〇 0.0220 0.0020 0.0011 0.40 2.60 1.0 〇 0.0017 0.3 0.40 1.49 1.0 Ο 0.0030 0.0009 0.2 0.017 0.40 1.90 1.0 〇 0.0029 0.0009 0,3 0.40 1.50 1.0 ο 0.0028 0.0009 0.2 0.05 0.40 1.42 1.0 ο 0.0023 0.0009 0.2 0.037 0.41 1.58 1.1 〇 0.0018 0.0012 0.4 0.39 1.16 0.9 〇 0.0020 0.0009 0.3 0.39 1.07 0.9 〇 0.0015 0.0035 0.4 0.41 1.24 1.1 〇 0.36 0.99 I 0.6 ΟClassification REM 〇8 Cu Cr Mo V Ceq Ni / Mn 10 x Ceq -3 Judgment * 0.37 1.22 0.7 〇0.36 3.46 0.6 〇0.36 0.64 0.6 〇0.37 2.96 0.7 〇0.36 0.99 0.6 〇0.36 1.32 0.6 〇0.38 0.92 0.8 〇0.39 1.89 0.9 〇0.39 1.16 0.9 〇0.38 1.39: 0.8 〇0,38 1.65 0.8 〇0.40 1.13 1.0 〇0.41 2.16 1.1 〇0.40 1.07 1.0 〇0.41 1.58 1.1 〇0.41 2.31 1.1 〇Inventive steel 0.41 1.68 1.1 〇0.41 1.35 1.1 〇0.40 1.13 1.0 〇 0.0012 0.40 1.14 1.0 〇0.4 ΟΛΟ 1.40 1.0 〇0.0023 0.2 0.41 1.62 1.1 〇0.0019 0.40 1.37 1.0 〇0.0019 0.0008 0.40 1.14 1.0 〇0.0017 0.0009 0.40 1.75 1.0 〇0.0220 0.0020 0.0011 0.40 2.60 1.0 〇0.0017 0.3 0.40 1.49 1.0 〇 0.0030 0.0009 0.2 0.017 0.40 1.90 1.0 〇0.0029 0.0009 0,3 0.40 1.50 1.0 ο 0.0028 0.0009 0.2 0.05 0.40 1.42 1 .0 ο 0.0023 0.0009 0.2 0.037 0.41 1.58 1.1 〇 0.0018 0.0012 0.4 0.39 1.16 0.9 〇 0.0020 0.0009 0.3 0.39 1.07 0.9 〇 0.0015 0.0035 0.4 0.41 1.24 1.1 〇 0.36 0.99 I 0.6 〇

20 200538561 表1之220 200538561 Table 1 of 2

區分 記號 c Si Μη Ρ S Ni Nb Al Ti Ν Ca Mg 發明鋼 D36 0.0S 0.19 1.21 0.010 0.003 1.5 0.015 0.015 0.008 0.0035 D37 0.10 0.19 1.11 0.006 0.002 1.9 0.0151 0.035 0.007 0.0035 D38 0.11 0.14 0.91 0.006 0.003 1.7 0.031 0.014 0.008 0.0035 D39 0.12 0.14 1.11 0.008 0.002 1.8 0.029 0.032 0.007 0.0032 D40 0.10 0.14 1.21 0.009 0.002 1.6 0.030 0.014 0.006 0.0037 D41 0.10 0.24 1.21 0.006 0.002 1.5 0.031 0.028 0.006 0.0042 D42 0.08 0.24 1.31 0.005 0.003 1.6 0.032 0.014 0.006 0.0035 D43 0.03 0.22 1.31 0.008 0.0031 2.5 0.035 0.038 0.006 0.0035 D44 0.06 0.24 0.81 0.007 0.003 3,2 0.035 0.014 0.009 0.0035 D45 0.03 0.11 1.51 0.007 0.002 1.8 0.035 0.014 0.010 0.0035 D46 0.07 0.11 1.21 0.007 0.003 1.4 0.028 0.014 0.009 0.0032 0.0015 D47 0.07 0.28 1.21 0.007 0.003 1.4 0.028 0.014 0.009 0.0032 0Ό015 D48 0.06 0.11 1.20 0.008 0.004 1.8 0.005 0.014 0.006 0.0035 0.0018 D49 0.06 0.28 1.20 0.008 0.004 1.8 0.005 0.014 0.006 0,0035 0.0017 比較鋼 C1 0.04 0.14 1.90 0.007 0.002 0.1 0.008 0.012 0.008 0.0032 C2 0.04 α〇9 Κ60 0.006 0.003 0.8 0.009 0.019 0.008 0.0037 C3 0.06 0.09 1.70 0.007 0.003 0.2 0.005 0.012 0.008 0.0042 C4 0.09 0.11 1.60 0.008 0.003 0.0 0.006 0.015 0.007 0.0035 C5 0.10 0.14 1.30 0.008 0.002 0.7 0.005 0.014 0.008 0.0035 G6 0.13 0.22 1.20 0.007 0.002 0.5 0.003 0.012 0.008 0.0035 C7 0.06 0.11 1.90 0.007 0.002 0.1 0.006 0,015 0.008 0.0035 C8 0.06 0.14 1.60 G.007 0、004 0.8 0.005 0.014 0Ό07 0.0032 C9 0.09 0.17 1.40 0.008 0.002 0.9 0.005 0.014 0.008 0.0037 C10 0.11 0.23 1.30 0.007 0.002 0.8 0.006 0.015 0.007 0.0042 C11 0.06 0.16 2.00 0.008 0.004 0.1 0.005 0.014 0.006 0.0035 C12 0.06 0.11 1.60 0.007 0.002 1.1 0.006 0.015 0.006 0.0035 C13 0.10 0.25 1.70 0.006 0.003 0.2 0.006 0.015 0.006 0.0035 C14 0.12 0.14 1.40 0.007 0.002 0.7 0,005 0.014 0.006 0.0035 C15 0.09 0.12 1.60 0.008 0.003 0.8 0.015 0.013 0.009 0.0032 C16 0.08 0.24 1.50 0.008 0.003 0.6 0.035 0.013 0.010 0.0037 C17 0.09 0.14 1.20 0.007 0.002 1.4 0.045 0.014 0.008 0.0042Distinguishing symbol c Si Μη Ρ S Ni Nb Al Ti Ν Ca Mg Invention steel D36 0.0S 0.19 1.21 0.010 0.003 1.5 0.015 0.015 0.008 0.0035 D37 0.10 0.19 1.11 0.006 0.002 1.9 0.0151 0.035 0.007 0.0035 D38 0.11 0.14 0.91 0.006 0.003 1.7 0.031 0.014 0.008 0.0035 D39 0.12 0.14 1.11 0.008 0.002 1.8 0.029 0.032 0.007 0.0032 D40 0.10 0.14 1.21 0.009 0.002 1.6 0.030 0.014 0.006 0.0037 D41 0.10 0.24 1.21 0.006 0.002 1.5 0.031 0.028 0.006 0.0042 D42 0.08 0.24 1.31 0.005 0.003 1.6 0.032 0.014 0.006 0.0035 D43 0.03 0.22 1.31 0.008 0.0031 0.0031 2.5 0.035 0.038 0.006 0.0035 D44 0.06 0.24 0.81 0.007 0.003 3,2 0.035 0.014 0.009 0.0035 D45 0.03 0.11 1.51 0.007 0.002 1.8 0.035 0.014 0.010 0.0035 D46 0.07 0.11 1.21 0.007 0.003 1.4 0.028 0.014 0.00 0.0032 0.0015 0.0047 D47 0.07 0.28 1.21 0.007 0.003 1.4 0.028 0.014 0.009 0.0032 0Ό015 D48 0.06 0.11 1.20 0.008 0.004 1.8 0.005 0.014 0.006 0.0035 0.0018 D49 0.06 0.28 1.20 0.008 0.004 1.8 0.005 0.014 0.006 0,0035 0.0017 Compare steel C1 0.04 0.14 1.90 0.0 07 0.002 0.1 0.008 0.012 0.008 0.0032 C2 0.04 α〇9 Κ60 0.006 0.003 0.8 0.009 0.019 0.008 0.0037 C3 0.06 0.09 1.70 0.007 0.003 0.2 0.005 0.012 0.008 0.0042 C4 0.09 0.11 1.60 0.008 0.003 0.0 0.006 0.015 0.007 0.0035 0.005 C5 0.10 0.14 1.30 0.008 0.002 0.7 0.005 0.014 0.008 0.0035 G6 0.13 0.22 1.20 0.007 0.002 0.5 0.003 0.012 0.008 0.0035 C7 0.06 0.11 1.90 0.007 0.002 0.1 0.006 0,015 0.008 0.0035 C8 0.06 0.14 1.60 G.007 0, 004 0.8 0.005 0.014 0Ό07 0.0032 C9 0.09 0.17 1.40 0.008 0.002 0.9 0.005 0.014 0.008 0.0037 C10 0.11 0.23 1.30 0.007 0.002 0.8 0.006 0.015 0.007 0.0042 C11 0.06 0.16 2.00 0.008 0.004 0.1 0.005 0.014 0.006 0.0035 C12 0.06 0.11 1.60 0.007 0.002 1.1 0.006 0.015 0.006 0.0035 C13 0.10 0.25 1.70 0.006 0.003 0.2 0.006 0.015 0.006 0.0035 C14 0.12 0.14 1.40 0.007 0.002 0.7 0,005 0.014 0.006 0.0035 C15 0.09 0.12 1.60 0.008 0.003 0.8 0.015 0.013 0.009 0.0032 C16 0.08 0.24 1.50 0.008 0.003 0.6 0.035 0.013 0.010 0.0037 C17 0.09 0.14 1.20 0.007 0.002 1.4 0.045 0.014 0.008 0.0042

21 200538561 表1之3 區分 REM 〇 3 Cu Cr Mo V Ceq Ni/Μπ 10 x Ceq -3 判定* 發明鋼 0.03 0.40 1.24 1.0 〇 0.41 1.71 1.1 0 0.045 0.38 1.87 0.8 〇 0.43 1.62 1.3 〇 0.2 0.42 1.32 1.2 〇 0.40 1.24 1.0 〇 0.41 1.22 1.1 〇 0.42 1.91 1.2 〇 0.41 3.95 1.1 〇 0.40 1.19 1Ό 〇 0.0018 0.4 0.39 1.16 0.9 〇 0.0018 0.4 0.39 1.16 0.9 〇 0.0026 0.0012 0.3 0.40 1.50 1.0 〇 0.0026 0.0012 0.3 0.40 1.50 K0 〇 比較鋼 0.36 0.05 0.6 X 0.36 0.50 0.6 X 0.36 0.12 0.6 X 0.36 0.00 0.6 X 0.36 0.54 0.6 X 0.36 0.42 0.6 X 0.38 0.05 0.8 X 0.38 0.50 0.8 X 0.38 0.64 0.8 X 0.38 0.62 0.8 X 0.40 0.05 1.0 X 0.40 0.69 1.0 X 0.40 0.12 1.0 X 0.40 0.50 1.0 X 0.41 0.50 1.1 X 0.37 0.40 0.7 X 0.38 1.17 0.8 〇21 200538561 Table 1 of 3 Differentiate REM 〇3 Cu Cr Mo V Ceq Ni / Μπ 10 x Ceq -3 Judgment * Invention steel 0.03 0.40 1.24 1.0 〇0.41 1.71 1.1 0 0.045 0.38 1.87 0.8 〇0.43 1.62 1.3 〇0.2 0.42 1.32 1.2 〇 0.40 1.24 1.0 〇0.41 1.22 1.1 〇0.42 1.91 1.2 〇0.41 3.95 1.1 〇0.40 1.19 1Ό 〇0.0018 0.4 0.39 1.16 0.9 〇0.0018 0.4 0.39 1.16 0.9 〇0.0026 0.0012 0.3 0.40 1.50 1.0 〇0.0026 0.0012 0.3 0.40 1.50 K0 〇Comparative steel 0.36 0.05 0.6 X 0.36 0.50 0.6 X 0.36 0.12 0.6 X 0.36 0.00 0.6 X 0.36 0.54 0.6 X 0.36 0.42 0.6 X 0.38 0.05 0.8 X 0.38 0.50 0.8 X 0.38 0.64 0.8 X 0.38 0.62 0.8 X 0.40 0.05 1.0 X 0.40 0.69 1.0 X 0.40 0.12 1.0 X 0.40 0.50 1.0 X 0.41 0.50 1.1 X 0.37 0.40 0.7 X 0.38 1.17 0.8

*滿足N i /Μ n g 1 Ο X C e Q — 3者記爲〇,不滿足者記爲X.* Those who satisfy N i / Μ n g 1 〇 X C e Q — 3 are recorded as 0, those who are not satisfied are recorded as X.

22 200538561 表222 200538561 Table 2

區分 記號 製造方法 板厚(mm) 母g 3(t/2部)u 氧化物數2) (個/mm2) 拉伸強度(MPa) 降伏應力(Mpa) vE-4。(J) 發明鋼 D1 TMCP 60 576 476 231 D2 TMCP 65 565 465 229 D3 DO-T 70 576 456 225 D4 TMCP 60 576 476 231 D5 D〇- T 55 605 485 238 D6 TMCP 65 565 465 229 D7 TMCP 70 560 460 219 D8 TMCP 80 541 441 213 D9 DQ -T 60 601 481 225 D10 TMCP 65 570 470 223 D11 TMCP 75 550 450 216 D12 TMCP 80 545 445 208 D13 TMCP 55 596 496 224 D14 DQ-T 65 595 475 217 D15 TMCP 70 566 466 213 D16 TMCP 65 578 478 214 D17 DQ-T 70 .588 468 211 D18 TMCP 75 556 456 210 D19 TMCP 70 565 465 214 D20 TMCP 70 575 482 214 D21 DQ-T 70 585 465 214 D22 TMCP 70 566 466 213 D23 TMCP 65 575 475 218 900 D24 DQ-T 60 605 485 221 1200 D25 TMCP 70 565 465 214 1300 D26 TMCP 80 545 445 209 1100 D27 TMCP 70 565 465 214 900 D28 TMCP 65 574 474 218 1800 D29 TMCP 60 585 485 221 2100 D30 DOT 65 594 474 218 2400 D31 TMCP 60 587 487 219 1900 D32 TMCP 70 563 463 217 700 D33 TMCP 65 572 472 221 600 D34 DQ-T 80 567 447 207 1400 D35 TMCP 70 555 455 225Classification Symbol Manufacturing method Plate thickness (mm) Female g 3 (t / 2) u Number of oxides 2) (pieces / mm2) Tensile strength (MPa) Drop stress (Mpa) vE-4. (J) Inventive steel D1 TMCP 60 576 476 231 D2 TMCP 65 565 465 229 D3 DO-T 70 576 456 225 D4 TMCP 60 576 476 231 D5 D〇- T 55 605 485 238 D6 TMCP 65 565 465 229 D7 TMCP 70 560 460 219 D8 TMCP 80 541 441 213 D9 DQ -T 60 601 481 225 D10 TMCP 65 570 470 223 D11 TMCP 75 550 450 216 D12 TMCP 80 545 445 208 D13 TMCP 55 596 496 224 D14 DQ-T 65 595 475 217 D15 TMCP 70 566 466 213 D16 TMCP 65 578 478 214 D17 DQ-T 70 .588 468 211 D18 TMCP 75 556 456 210 D19 TMCP 70 565 465 214 D20 TMCP 70 575 482 214 D21 DQ-T 70 585 465 214 D22 TMCP 70 566 466 213 D23 TMCP 65 575 475 218 900 D24 DQ-T 60 605 485 221 1200 D25 TMCP 70 565 465 214 1300 D26 TMCP 80 545 445 209 1100 D27 TMCP 70 565 465 214 900 D28 TMCP 65 574 474 218 1800 D29 TMCP 60 585 485 221 2100 D30 DOT 65 594 474 218 2400 D31 TMCP 60 587 487 219 1900 D32 TMCP 70 563 463 217 700 D33 TMCP 65 572 472 221 600 D34 DQ-T 80 567 447 207 1400 D35 TMCP 70 555 455 225

23 200538561 表2之123 200538561 Table 1 of 2

對接]回焊接條件 3) FL〜HA21mm 的 4) 平均r粒徑(/i m) HAZ韌性5) 區分 焊接方法 入熱(kJ/mm) FL/vE^0 (J) FL+1 mm/vE.40 (J) EGW 39 480 140 128 EGW 42 520 135 124 ESW 85 770 116 106 ESW 73 660 123 113 ESW 67 605 127 117 EGW 42 520 135 124 ESW 85 770 116 106 EGW 51 640 124 114 EGW 39 480 140 128 ESW 79 715 119 109 EGW 48 600 128 117 EGW 51 640 124 114 EGW 35 440 144 132 ESW 79 715 119 109 ESW 85 770 116 106 EGW 42 520 135 124 發明鋼 EGW 45 560 131 120 EGW 48 600 128 117 EGW 45 560 131 120 EGW 45 560 171 156 ESW 85 770 116 106 EGW 45 560 184 180 ESW 79 180 207 189 EGW 39 165 214 196 EGW 45 152 221 203 EGW 51 185 204 187 EGW 45 180 207 189 ESW 79 167 213 195 EGW 39 184 205 188 EGW 42 165 214 196 EGW 39 184 205 188 EGW 45 180 207 189 EGW 42 164 214 197 ESW 98 180 196 180 ESW 85 660 123 113Butt] Back welding conditions 3) FL ~ HA21mm 4) Average r particle size (/ im) HAZ toughness 5) Differentiating welding method heat (kJ / mm) FL / vE ^ 0 (J) FL + 1 mm / vE. 40 (J) EGW 39 480 140 128 EGW 42 520 135 124 ESW 85 770 116 106 ESW 73 660 123 113 ESW 67 605 127 117 EGW 42 520 135 124 ESW 85 770 116 106 EGW 51 640 124 114 EGW 39 480 140 128 ESW 79 715 119 109 EGW 48 600 128 117 EGW 51 640 124 114 EGW 35 440 144 132 ESW 79 715 119 109 ESW 85 770 116 106 EGW 42 520 135 124 Invention steel EGW 45 560 131 120 EGW 48 600 128 117 EGW 45 560 131 120 EGW 45 560 171 156 ESW 85 770 116 106 EGW 45 560 184 180 ESW 79 180 207 189 EGW 39 165 214 196 EGW 45 152 221 203 EGW 51 185 204 187 EGW 45 180 207 189 ESW 79 167 213 195 EGW 39 184 205 188 EGW 42 165 214 196 EGW 39 184 205 188 EGW 45 180 207 189 EGW 42 164 214 197 ESW 98 180 196 180 ESW 85 660 123 113

24 200538561 表2之224 200538561 Table 2 of 2

區分 記號 製造方法 板厚(mm) 母; B(t/2部)&quot; 氧化物數a (個/mm〇 拉伸強度(MPa) 降伏應力(MPa) vE-4〇 &lt;J) 發明鋼 D36 DQ-T 70 584 464 215 D37 TMCP 65 578 478 214 D38 TMCP 60 581 481 226 D39 TMCP 70 571 471 208 D40 DQ - T 80 570 450 203 D41 TMCP 70 565 465 214 D42 TMCP 65 576 476 216 D43 TMCP 60 589 489 217 D44 TMCP 65 577 477 215 D45 DQ-T 60 605 485 221 D46 TMCP 70 553 465 217 900 D47 TMCP 70 579 481 217 400 D48 TMCP 60 578 485 221 2300 D49 TMCP 60 592 485 221 1500 比較鋼 G1 TMCP 70 556 456 225 C2 DQ-T 60 595 475 233 C3 TMCP 75 544 444 224 C4 TMCP 60 574 474 234 C5 TMCP 60 576 476 232 C6 TMCP 55 586 486 236 C7 DQ-T 60 601 481 226 C8 TMCP 60 580 480 227 C9 TMCP 60 581 481 226 C10 TMCP 60 580 480 227 C11 DQ-T 70 585 465 214 C12 TMCP 60 585 485 221 C13 TMCP 70 564 464 215 C14 TMCP 65 575 475 218 C15 TMCP 55 598 498 222 C16 DQ-T 65 588 468 226 C17 TMCP 60 581 481 226Manufacturing method of distinguishing marks Plate thickness (mm) Female; B (t / 2) &quot; Number of oxides a (piece / mm〇tensile strength (MPa) Drop stress (MPa) vE-4〇 &lt; J) Invention steel D36 DQ-T 70 584 464 215 D37 TMCP 65 578 478 214 D38 TMCP 60 581 481 226 D39 TMCP 70 571 471 208 D40 DQ-T 80 570 450 203 D41 TMCP 70 565 465 214 D42 TMCP 65 576 476 216 D43 TMCP 60 589 489 217 D44 TMCP 65 577 477 215 D45 DQ-T 60 605 485 221 D46 TMCP 70 553 465 217 900 D47 TMCP 70 579 481 217 400 D48 TMCP 60 578 485 221 2300 D49 TMCP 60 592 485 221 1500 Compare steel G1 TMCP 70 556 456 225 C2 DQ-T 60 595 475 233 C3 TMCP 75 544 444 224 C4 TMCP 60 574 474 234 C5 TMCP 60 576 476 232 C6 TMCP 55 586 486 236 C7 DQ-T 60 601 481 226 C8 TMCP 60 580 480 227 C9 TMCP 60 581 481 226 C10 TMCP 60 580 480 227 C11 DQ-T 70 585 465 214 C12 TMCP 60 585 485 221 C13 TMCP 70 564 464 215 C14 TMCP 65 575 475 218 C15 TMCP 55 598 498 222 C16 DQ-T 65 588 468 226 C17 TMCP 60 581 481 226

25 200538561 表2之3 對接1回焊接條件 3) FL〜HAZlmm的 4) HAZ韌性5) 區分 焊接方法 入熱(kJ/mm) 平均r粒徑(ym) FL/vE_40 (J) FL+1mm/vE_4〇 (J) ESW 85 605 127 117 EGW 42 520 135 124 ESW 73 770 116 106 EGW 45 640 124 114 EGW 51 480 140 128 ! ESW 85 715 119 109 發明鋼 EGW 42 600 128 117 EGW 39 640 124 114 EGW 42 440 144 : 132 ESW 73 715 119 109 EGW 45 145 225 206 EGW 45 195 200 183 EGW 39 164 214 236 EGW 39 185 204 225 ESW 85 770 36 25 EGW 39 480 57 40 EGW 48 600 46 32 EGW 39 480 57 40 EGW 39 480 57 40 ESW 67 605 45 32 EGW 39 480 57 40 EGW 39 480 57 40 比較鋼 EGW 39 480 57 40 EGW 39 480 57 40 ESW 85 770 36 25 EGW 39 480 57 40 EGW 45 560 49 34 EGW 42 520 53 37 ESW 67 605 45 32 EGW 42 520 53 37 EGW 39 480 57 40 1) 板厚中心位置、YS與TS是2片試驗片的平均值,-40°c下 的查拜式吸收能(vE-40)是3片試驗片的平均值。25 200538561 Table 2-3 Welding conditions for 1 butt joint 3) FL to HAZlmm 4) HAZ toughness 5) Differentiating welding method heat (kJ / mm) average r particle size (ym) FL / vE_40 (J) FL + 1mm / vE_4〇 (J) ESW 85 605 127 117 EGW 42 520 135 124 ESW 73 770 116 106 EGW 45 640 124 114 EGW 51 480 140 128! ESW 85 715 119 109 Invention steel EGW 42 600 128 117 EGW 39 640 124 114 EGW 42 440 144: 132 ESW 73 715 119 109 EGW 45 145 225 206 EGW 45 195 200 183 EGW 39 164 214 236 EGW 39 185 204 225 ESW 85 770 36 25 EGW 39 480 57 40 EGW 48 600 46 32 EGW 39 480 57 40 EGW 39 480 57 40 ESW 67 605 45 32 EGW 39 480 57 40 EGW 39 480 57 40 Comparative steel EGW 39 480 57 40 EGW 39 480 57 40 ESW 85 770 36 25 EGW 39 480 57 40 EGW 45 560 49 34 EGW 42 520 53 37 ESW 67 605 45 32 EGW 42 520 53 37 EGW 39 480 57 40 1) The center position of the plate thickness, YS and TS are the average of 2 test pieces, and the Chabbit absorption energy (vE-40 at -40 ° c) ) Is an average of 3 test pieces.

2) 由鋼板的任意處製作抽提複製品。於電子顯微鏡以10000 倍觀察100視野以上(觀察面積為10000//m2以上)。 但,關於未滿0.1//m的粒子提高適當倍率觀察。 於投影面積直徑0.005〜0.5//m的粒子的元素分析中,計 算含氧化物者,換算成每1mm2的個數。 3) EGW :電氣焊接,ESW :電熔渣焊接,焊接入熱量為焊 10 接全長的平均值,於各焊接法中使用相同的焊接材料。 4) 被包含於含有以板厚中央部為中心的板厚方向2mm與 FL〜HAZlmm的面的舊沃斯田鐵晶粒的平均粒徑。 26 200538561 以截面法測定。將連結成網狀的肥粒鐵作為舊沃斯田鐵 晶粒的晶界進行測定 5)FL刻痕係將WM與HAZ等分地劃線,於各刻痕位置的 vE-40-是3片試驗片的平均值。 5 產業上之可利用性 本發明係提供一種可滿足船舶、海洋構造物、中高層 大樓等對破壞的嚴格的韌性要求之厚鋼板,對該產業領域 帶來的效果極大,進一步從構造物的安全性的意義上考 量,對社會的貢獻亦相當大。 10 【圖式簡單說明】 第1圖係顯示相當於45kJ/mm的焊接熱循環之圖。 第2圖係顯示Ni/Mn、Ceq、再現HAZ韌性之關係圖。 第3圖係顯示藉著分散微細氧化物或有效利用B使再現 HAZ韌性提高之效果之圖。 15 【主要元件符號說明】2) Make an extraction copy from anywhere on the steel plate. Observe 100 fields of view or more with an electron microscope at 10,000 times (observation area is 10000 // m2 or more). However, it is observed that the particles under 0.1 // m increase the appropriate magnification. In elemental analysis of particles having a projected area diameter of 0.005 to 0.5 // m, those containing oxides are calculated and converted to the number per 1 mm2. 3) EGW: electric welding, ESW: electric slag welding, the welding heat is the average value of the total length of the welding, and the same welding material is used in each welding method. 4) The average grain size of old Vostian iron crystal grains included in a plane having a plate thickness direction of 2 mm and a surface of FL to HAZ1 mm centered on the center of the plate thickness. 26 200538561 Measured by section method. The iron grains connected to the network were measured as the grain boundaries of the old Vostian iron grains. 5) FL scoring is to scribe WM and HAZ equally, and vE-40 at each scoring position is a 3-piece test. The average of the slices. 5 Industrial Applicability The present invention provides a thick steel plate that can meet the strict toughness requirements for damage such as ships, marine structures, and high-rise buildings. It has a great effect on the industry and further improves the safety of structures. Considered in the sense of sex, its contribution to society is also considerable. 10 [Brief Description of the Drawings] Figure 1 shows the welding thermal cycle equivalent to 45kJ / mm. Figure 2 is a graph showing the relationship between Ni / Mn, Ceq, and reproduced HAZ toughness. Fig. 3 is a graph showing the effect of improving the reproducibility of HAZ toughness by dispersing fine oxides or using B effectively. 15 [Description of main component symbols]

2727

Claims (1)

200538561 5200538561 5 10 1510 15 20 十、申請專利範圍: 1. 一種於大入熱焊接下的焊接熱影響部的低溫韌性優異之 高強度厚鋼板,含有以下元素,即: C : 0.03〜0.14 質量% ; Si : 0.30質量%以下; Μη : 0.8〜2.0質量% ; Ρ : 0.02質量%以下; S : 0.005質量%以下; Α1 : 0.001 〜0.040質量% ; Ν : 0.0010〜0.0100質量% ; Ni : 0.8〜4.0質量% ; Ti : 0.005〜0.030質量% ;及 Nb : 0.003〜0.040質量 % ; 且,Ni與Μη滿足下式〔1〕,即: Ni/Mn ^ 10xCeq-3(0.36 &lt; Ceq &lt; 0.42)〔1〕 但,Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15 又,剩餘為鐵及不可避免之雜質。 2. 如申請專利範圍第1項之於大入熱焊接下的焊接熱影響 部的低溫韌性優異之高強度厚鋼板,進一步包含有1種或 2種以上的以下元素,即: Ca : 0.0003〜0.0050質量 % ; Mg : 0.0003〜0.0050質量 % ;及 REM : 0.001 〜0.030質量% ; 且,含有Ο : 0.0010〜0.0050質量%及100個/mm2以上的投 28 20053856120 X. Scope of patent application: 1. A high-strength thick steel plate with excellent low-temperature toughness in a welded heat-affected zone under large-input heat welding, containing the following elements: C: 0.03 ~ 0.14 mass%; Si: 0.30 mass% The following; Mn: 0.8 to 2.0 mass%; P: 0.02 mass% or less; S: 0.005 mass% or less; A1: 0.001 to 0.040 mass%; Ν: 0.0010 to 0.0100 mass%; Ni: 0.8 to 4.0 mass%; Ti: 0.005 to 0.030% by mass; and Nb: 0.003 to 0.040% by mass; and Ni and Mn satisfy the following formula [1], namely: Ni / Mn ^ 10xCeq-3 (0.36 &lt; Ceq &lt; 0.42) [1] However, Ceq = C + Mn / 6 + (Cr + Mo + V) / 5 + (Ni + Cu) / 15 The rest is iron and inevitable impurities. 2. If the high-strength thick steel plate with excellent low-temperature toughness in the welded heat-affected zone under large-entry heat welding in item 1 of the scope of the patent application, further contains one or more of the following elements, namely: Ca: 0.0003 ~ 0.0050% by mass; Mg: 0.0003 to 0.0050% by mass; and REM: 0.001 to 0.030% by mass; and 〇: 0.0010 to 0.0050% by mass and 100 pieces / mm2 or more cast 28 200538561 10 1510 15 20 影面積直徑為0.005〜0.5//m的氧化物。 3. 如申請專利範圍第1項或第2項之於大入熱焊接下的焊接 熱影響部的低溫韌性優異之高強度厚鋼板,進一步含有 B : 0.0005〜0.0050質量%。 4. 如申請專利範圍第1項之於大入熱焊接下的焊接熱影響 部的低溫韌性優異之高強度厚鋼板,進一步含有1種或2 種以上的以下元素,即: Cr ·· 0.1 〜0.5 質量 % ; Mo : 0.01 〜0.5 質量% ; V ·· 0.005〜0.10質量% ;及 Cu : 0.1 〜1.0質量%。 5. 如申請專利範圍第2項之於大入熱焊接下的焊接熱影響 部的低溫韌性優異之高強度厚鋼板,進一步含有1種或2 種以上的以下元素,即: Cr : 0.1 〜0.5 質量 % ; Mo : 0.01 〜0.5 質量 % ; V : 0.005〜0.10質量 % ;及 Cu : 0.1 〜1.0質量%。 6. 如申請專利範圍第3項之於大入熱焊接下的焊接熱影響 部的低溫韌性優異之高強度厚鋼板,進一步含有1種或2 種以上的以下元素,即: Cr : 0.1 〜0.5 質量 % ; Mo ·· 0.01 〜0.5 質量% ; V ·· 0.005〜0.10質量% ;及 29 200538561 Cu : 0.1 〜1.0質量%。20 An oxide having a shadow area diameter of 0.005 to 0.5 // m. 3. For example, in the welding process under item 1 or 2 of the scope of patent application, the high-strength thick steel plate with excellent low-temperature toughness at the heat-affected zone, further containing B: 0.0005 to 0.0050 mass%. 4. For example, the high-strength thick steel plate with excellent low-temperature toughness in the welded heat-affected zone under large-entry heat welding in item 1 of the scope of the patent application, further contains one or more of the following elements, namely: Cr ·· 0.1 ~ 0.5% by mass; Mo: 0.01 to 0.5% by mass; V ·· 0.005 to 0.10% by mass; and Cu: 0.1 to 1.0% by mass. 5. If the high-strength thick steel plate with excellent low-temperature toughness in the welded heat-affected zone under large-entry heat welding in item 2 of the scope of patent application, further contains one or more of the following elements, namely: Cr: 0.1 to 0.5 % By mass; Mo: 0.01 to 0.5% by mass; V: 0.005 to 0.10% by mass; and Cu: 0.1 to 1.0% by mass. 6. If the high-strength thick steel plate with excellent low-temperature toughness in the welded heat-affected zone under large-entry heat welding in item 3 of the scope of patent application, further contains one or more of the following elements, namely: Cr: 0.1 to 0.5 Mass%; Mo .. 0.01 to 0.5 mass%; V .. 0.005 to 0.10 mass%; and 29 200538561 Cu: 0.1 to 1.0 mass%. 3030
TW094110988A 2004-04-07 2005-04-07 A high-strength thick steel plate excellent in low temperature toughness at heat affected zone resulting from large heat input welding TWI295693B (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2004113278 2004-04-07
JP2005102041A JP4660250B2 (en) 2004-04-07 2005-03-31 Thick high-strength steel sheet with excellent low-temperature toughness in the heat affected zone by high heat input welding

Publications (2)

Publication Number Publication Date
TW200538561A true TW200538561A (en) 2005-12-01
TWI295693B TWI295693B (en) 2008-04-11

Family

ID=35125101

Family Applications (1)

Application Number Title Priority Date Filing Date
TW094110988A TWI295693B (en) 2004-04-07 2005-04-07 A high-strength thick steel plate excellent in low temperature toughness at heat affected zone resulting from large heat input welding

Country Status (8)

Country Link
US (1) US20070181223A1 (en)
EP (1) EP1736562A4 (en)
JP (1) JP4660250B2 (en)
KR (1) KR100839262B1 (en)
NO (1) NO20065095L (en)
SG (1) SG151274A1 (en)
TW (1) TWI295693B (en)
WO (1) WO2005098068A1 (en)

Families Citing this family (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4901262B2 (en) * 2006-03-29 2012-03-21 新日本製鐵株式会社 Thick steel plate with excellent toughness of heat affected zone
JP4891836B2 (en) * 2007-05-09 2012-03-07 株式会社神戸製鋼所 Steel plate with excellent toughness of weld heat affected zone in high heat input welding
JP5096088B2 (en) * 2007-09-13 2012-12-12 株式会社神戸製鋼所 Welded joints with excellent toughness and fatigue cracking suppression properties
KR101018159B1 (en) * 2008-05-15 2011-02-28 주식회사 포스코 High-strength steel sheet with excellent low temperature toughness and manufacturing method thereof
KR100951296B1 (en) * 2007-12-04 2010-04-02 주식회사 포스코 Steel plate for linepipe having high strength and excellent low temperature toughness and manufacturing method of the same
CN101883875B (en) * 2007-12-04 2012-10-10 Posco公司 High-strength steel sheet with excellent low temperature toughness and manufacturing method thereof
CA2674197C (en) * 2007-12-07 2014-06-10 Nippon Steel Corporation Steel plate superior in ctod properties of weld heat-affected zone and method of production of same
TWI468529B (en) * 2009-04-27 2015-01-11 China Steel Corp High strength steels and components thereof for high welding heat welding
JP4700769B2 (en) 2009-05-19 2011-06-15 新日本製鐵株式会社 Steel for welding and method for manufacturing the same
TWI365915B (en) * 2009-05-21 2012-06-11 Nippon Steel Corp Steel for welded structure and producing method thereof
WO2012070355A1 (en) * 2010-11-22 2012-05-31 新日本製鐵株式会社 Electron-beam welded joint, steel material for electron-beam welding, and manufacturing method therefor
CN103221565B (en) * 2010-11-22 2016-04-27 新日铁住金株式会社 Electro-beam welding joint and electrons leaves welding steel plate and its manufacture method
KR20120075274A (en) * 2010-12-28 2012-07-06 주식회사 포스코 High strength steel sheet having ultra low temperature toughness and method for manufacturing the same
JP5612532B2 (en) * 2011-04-26 2014-10-22 株式会社神戸製鋼所 Steel sheet excellent in low temperature toughness and weld joint fracture toughness and method for producing the same
JP5811044B2 (en) * 2012-06-13 2015-11-11 新日鐵住金株式会社 Thick high-strength steel sheet excellent in weldability and weld heat-affected zone toughness and method for producing the same
WO2014199488A1 (en) * 2013-06-13 2014-12-18 新日鐵住金株式会社 Ultrahigh-tensile-strength steel plate for welding
JP5713135B1 (en) 2013-11-19 2015-05-07 新日鐵住金株式会社 steel sheet
CN103898418B (en) * 2014-03-07 2016-05-04 舞阳钢铁有限责任公司 Large thickness Ni is low-temperature (low temperature) vessel steel plate and production method thereof
CN103938065B (en) * 2014-04-22 2015-10-28 钢铁研究总院 In a kind of high input energy welding steel, compound adds the method for magnesium titanium
CN105039865B (en) * 2015-08-26 2017-07-14 江苏省沙钢钢铁研究院有限公司 A kind of high-strength high-toughness steel plate and its manufacture method
JP7260780B2 (en) * 2019-06-17 2023-04-19 日本製鉄株式会社 High strength steel plate for high heat input welding
JP7260779B2 (en) * 2019-06-17 2023-04-19 日本製鉄株式会社 High strength steel plate for high heat input welding
CN113186466B (en) * 2021-04-27 2022-05-17 江苏省沙钢钢铁研究院有限公司 Low-temperature steel bar and production method thereof

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2760713B2 (en) * 1992-09-24 1998-06-04 新日本製鐵株式会社 Method for producing controlled rolled steel with excellent fire resistance and toughness
JPH093597A (en) * 1995-06-21 1997-01-07 Nippon Steel Corp Steel for low temperature use excellent in toughness of weld heat affected zone and its production
JP3749616B2 (en) * 1998-03-26 2006-03-01 新日本製鐵株式会社 High-strength steel for welding with excellent toughness of heat affected zone
JPH11293383A (en) * 1998-04-09 1999-10-26 Nippon Steel Corp Thick steel plate minimal in hydrogen induced defect, and its production
EP1221493B1 (en) * 2000-05-09 2005-01-12 Nippon Steel Corporation THICK STEEL PLATE BEING EXCELLENT IN CTOD CHARACTERISTIC IN WELDING HEAT AFFECTED ZONE AND HAVING YIELD STRENGTH OF 460 Mpa OR MORE
JP2003313628A (en) * 2002-04-22 2003-11-06 Nippon Steel Corp Steel product superior in toughness of weld heat- affected zone

Also Published As

Publication number Publication date
EP1736562A1 (en) 2006-12-27
KR20060130700A (en) 2006-12-19
JP4660250B2 (en) 2011-03-30
EP1736562A4 (en) 2007-10-10
US20070181223A1 (en) 2007-08-09
JP2005320624A (en) 2005-11-17
SG151274A1 (en) 2009-04-30
KR100839262B1 (en) 2008-06-17
TWI295693B (en) 2008-04-11
NO20065095L (en) 2007-01-03
WO2005098068A1 (en) 2005-10-20

Similar Documents

Publication Publication Date Title
TW200538561A (en) A high-strength thick steel plate excellent in low temperature toughness at heat affected zone resulting from large heat input welding
JP5162382B2 (en) Low yield ratio high toughness steel plate
JP5397363B2 (en) Thick high-strength steel sheet with excellent low-temperature toughness in the heat affected zone by high heat input welding
JP5076658B2 (en) Steel material for large heat input welding
WO2010134220A1 (en) Steel material for high heat input welding
JP6245417B1 (en) Steel
JP2009127069A (en) High toughness steel plate for line pipe, and its manufacturing method
KR20160127808A (en) High-tensile-strength steel plate and process for producing same
TWI589708B (en) Steel material for high heat input welding
JP4891836B2 (en) Steel plate with excellent toughness of weld heat affected zone in high heat input welding
WO2013077022A1 (en) Steel material for welding
JP4041447B2 (en) Thick steel plate with high heat input welded joint toughness
JP2009235548A (en) Low yield ratio high tensile strength thick steel plate having excellent toughness in super-large heat input weld affected zone, and method for producing the same
JP4341395B2 (en) High strength steel and weld metal for high heat input welding
JP4949210B2 (en) Steel excellent in toughness of weld heat-affected zone and method for producing the same
WO2016009595A1 (en) Method of manufacturing steel plate for high-heat input welding
TW201538746A (en) Steel material for welding
JP4276576B2 (en) Thick high-strength steel sheet with excellent heat input and heat-affected zone toughness
JP2009235549A (en) Method for producing low yield ratio high tension thick steel plate excellent in toughness at super-high heat input welding affected part
JPWO2019050010A1 (en) Steel sheet and manufacturing method thereof
JP6226163B2 (en) High-tensile steel plate with excellent low-temperature toughness in heat affected zone and its manufacturing method
JP4673788B2 (en) Steel excellent in toughness of weld heat-affected zone and method for producing the same
JP5888119B2 (en) Thick steel plate with excellent HAZ toughness
JP2017193756A (en) Thick steel sheet
CN116171335A (en) Steel plate

Legal Events

Date Code Title Description
MM4A Annulment or lapse of patent due to non-payment of fees