JPS613833A - Manufacture of high strength steel with superior weldability - Google Patents
Manufacture of high strength steel with superior weldabilityInfo
- Publication number
- JPS613833A JPS613833A JP12444284A JP12444284A JPS613833A JP S613833 A JPS613833 A JP S613833A JP 12444284 A JP12444284 A JP 12444284A JP 12444284 A JP12444284 A JP 12444284A JP S613833 A JPS613833 A JP S613833A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- less
- temperature
- low
- strength
- Prior art date
- Legal status (The legal status 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 status listed.)
- Granted
Links
Classifications
-
- 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
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は高強度鋼の製造方法に関するもので、商い強度
と良好な溶接性が必要な圧力容器、橋梁および建設機械
等の溶接構造用材料として有用な鋼に関するものである
。Detailed Description of the Invention (Industrial Application Field) The present invention relates to a method for manufacturing high-strength steel, which is a material for welded structures such as pressure vessels, bridges, and construction machinery that require high strength and good weldability. It relates to steel useful as
（従来の技術）
従来、上記用途の高強度鋼はオフライン焼入れ、焼戻し
熱処理法によシ製造されている。しかしながら、これら
の鋼には高強度を得るため多種多量の合金元素が添加さ
れるため製造コストが高いと共に溶接割れ防止のため溶
接時には高い温度の予熱が必峻である。(Prior Art) Conventionally, high-strength steel for the above-mentioned uses has been manufactured by off-line quenching and tempering heat treatment. However, in order to obtain high strength, many types of alloying elements are added to these steels, which results in high manufacturing costs and requires preheating to a high temperature during welding to prevent weld cracking.
従来提案されたものとして特公昭４１−２７６３号公報
記載の方法が公知である。これはＭＯとＮｂを共存させ
ることによりＭｏ−Ｎｂ系の析出物により、析出硬化を
利用し高強度を付与するものである。As a conventionally proposed method, a method described in Japanese Patent Publication No. 41-2763 is known. This is to provide high strength by making use of precipitation hardening due to Mo-Nb based precipitates by allowing MO and Nb to coexist.
そして、これはすべてオフラインで通常の焼入れ、焼戻
し熱処理によって製造することが前捉となっている。こ
の場合焼入れ温度は９００℃前後であるので、十分な析
出硬化をはかるために多くのＮｂおよびＭｏの添加が必
要となり、コスト高になると共に、溶接性、特に溶接割
れ性に問題があり溶接時に高い温度の予熱が必要でその
改善が強く望まれていた。The idea is to manufacture all of these off-line through normal quenching and tempering heat treatment. In this case, the quenching temperature is around 900°C, so it is necessary to add a large amount of Nb and Mo to achieve sufficient precipitation hardening, which increases costs and causes problems with weldability, especially weld cracking. Preheating at a high temperature is required, and an improvement in this has been strongly desired.
（発明が解決しようとする問題点）
本発明はこのような用途に必要な高度の靭性と良好な溶
接性、なかんずく溶接割れ性を有し、しかも引張強さ８
０ ｋｇｆ／ｍ２以上の高強度を有する５４を５０調を
越える厚い板厚まで安価に製造する方法を提供するもの
である。(Problems to be Solved by the Invention) The present invention has a high degree of toughness and good weldability necessary for such uses, and above all, weld cracking resistance, and has a tensile strength of 8.
The purpose of the present invention is to provide a method for inexpensively manufacturing 54 having a high strength of 0 kgf/m2 or more to a thickness exceeding 50 scale.
（問題点を解決するための手段）
本発明者らはこのような目的を有利に達成するために炭
素当量を低くして且つ８０ ｋｇ ｆ ／ｍａ２ 以上
の高強度および高靭性を得るための鋼の製造方法につい
て種々検討した結果、Ｎｂ ｔ Ｍｏ ＊ Ｂおよび低
Ｎを組み合わせた鋼をオンライン焼入れし、その後焼戻
すことにより、低炭素当量できわめてすぐれた特性を有
する高靭性、高強度鋼が得られることを知見した。(Means for Solving the Problems) In order to advantageously achieve these objectives, the present inventors have developed a steel that has a low carbon equivalent and has high strength and toughness of 80 kg f /ma2 or more. As a result of various studies on manufacturing methods, we found that by on-line quenching a steel that combines Nb t Mo * B and low N, and then tempering it, a high-toughness, high-strength steel with a low carbon equivalent and extremely excellent properties can be obtained. I found out that it can be done.
本発明はこのような知見をもとに構成したものでその要
旨とするところは、
重量％にてＣ：０．０４〜０．１１％、Ｓｉ：１．０％
以下。The present invention was constructed based on such knowledge, and its gist is as follows: C: 0.04-0.11%, Si: 1.0% in weight%
below.
Ｍｎ ： ０．５’Ｏ〜２．００％、 Ｍｏ ：０
． ｉ’ ０〜１．０ ’％ 。Mn: 0.5'O~2.00%, Mo: 0
．． i'0-1.0'%.
Ｎｂ ： ０．００５〜０．０５％、Ｂ：０．０１−以
下。Nb: 0.005-0.05%, B: 0.01- or less.
Ａｔ ： ０．１％以下 、Ｎ ： ０．００６
０チ以下。At: 0.1% or less, N: 0.006
Less than 0 chi.
を基本成分とし、必要に応じて Ｃｒ ： １％以下 、 Ｎｉ ： １％以下。as the basic ingredients, and as necessary Cr: 1% or less, Ni: 1% or less.
Ｃｕ ： １％以下 、Ｖ：０．１％以下。Cu: 1% or less, V: 0.1% or less.
Ｃａ：０．０１％以下のうち１種または２種以上を含有
し残部Ｆｓおよび不可避不純物よりなる鋼を加熱温度１
０００℃以上、圧延終了温度８００℃以上の条件で加熱
圧延し、圧延後直ちに２００℃以下まで急冷した後Ａｃ
１以下で焼戻し熱処理を施こすことを特徴とする溶接性
にすぐれた高強度鋼の製造方法にある。A steel containing one or more of Ca: 0.01% or less and the balance Fs and unavoidable impurities was heated to a temperature of 1.
Ac
The present invention provides a method for producing high-strength steel with excellent weldability, characterized by subjecting it to tempering heat treatment at a temperature of 1 or less.
（発明の作用）
本発明者らは種々の実験・検討を重ねた結果、適切なＮ
ｂ −Ｍｏ −Ｂ−Ｎ成分系をオンライン焼入れした後
、焼戻すことによりＭ、−Ｎｂ系析出物の析出硬化を飛
躍的に活用することが可能であると共に、ＢおよびＭｏ
の焼入性向上効果を著しく高めることが可能であること
を見出した。即ち本発明はオンライン加熱時のＮｂおよ
びＭｏの固溶により少量のＮｂ量でオンライン急冷後の
焼戻し時に従来予想できないほどの著しい析出硬化を生
じることおよび低Ｎ化をはかることによシ、この少量の
Ｎｉ）がＢの焼入性を大きく高めると共に％Ｍｏの焼入
性向上効果と複合して著しい焼入性向上がはかれること
の２つの知見を得たことに基づいている。(Operation of the invention) As a result of various experiments and studies, the present inventors found that an appropriate N.
b By on-line quenching and then tempering the -Mo -B-N component system, it is possible to dramatically utilize the precipitation hardening of M, -Nb system precipitates, and also to
It has been found that it is possible to significantly enhance the hardenability improvement effect of That is, the present invention is capable of producing significant precipitation hardening that could not previously be expected during tempering after on-line quenching with a small amount of Nb due to solid solution of Nb and Mo during on-line heating, and by aiming to reduce the amount of Nb. This is based on the two findings that %Ni) greatly improves the hardenability of B and combines with the hardenability improving effect of %Mo to significantly improve hardenability.
この方法によって、比較的少ない化学成分で良好な低温
靭性・溶接性を有する８０ｋｇｆ／ｍ 以上の引張強
さを有する鋼の製造を可能としたものであり、特に板厚
５０ｍを越える厚肉材の製造も可能である。This method makes it possible to manufacture steel with a tensile strength of 80 kgf/m or more, which has good low-temperature toughness and weldability with relatively few chemical components, and is especially suitable for thick-walled materials exceeding 50 m in thickness. Manufacturing is also possible.
次に、本発明における対象鋼の化学成分の限定理由につ
いて述べる。Next, the reason for limiting the chemical composition of the target steel in the present invention will be described.
Ｃは高強度鋼を得るために０．０４１以上は必要である
が、含有量が多くなる程強度が上昇するが、低温靭性が
低下すると共に耐溶接割れ性が劣化するのでその含有量
を０．０４〜０．１１％とする。C is required to be at least 0.041 in order to obtain high-strength steel, and as the content increases, the strength increases, but low-temperature toughness and weld cracking resistance deteriorate, so the content should be reduced to 0. .04 to 0.11%.
Ｓｔは通常脱酸元素として存在するが強度向上のため０
．１％以上は必要である。しかし、１．０チを超えると
低温靭性の低下が著しいため上限は１．０チとする。St usually exists as a deoxidizing element, but it is omitted to improve strength.
．． 1% or more is necessary. However, if it exceeds 1.0 inch, the low-temperature toughness deteriorates significantly, so the upper limit is set at 1.0 inch.
Ｍｎは高強度を？４るために０．５０％以上は必要であ
るが２．０チを１６えると低温靭性・溶接性を損うので
その含有量を０．５０〜２．０チとする。Does Mn have high strength? Although 0.50% or more is necessary to achieve 4.4% of copper, the content is set at 0.50 to 2.0% since low-temperature toughness and weldability will be impaired if 16% of 2.0% is added.
Ｍ、は強度・低温靭性の向上に有用であるが、０．１％
未満では効果が小さい。他方、１％を超えると強度が高
くｆｒ、ｐすぎ、低温靭性の低下を招くと共に高価にな
るため０．１−１．０ ％とする。望ましくは’０．２
５〜０．６％である。M is useful for improving strength and low-temperature toughness, but 0.1%
If it is less than that, the effect will be small. On the other hand, if it exceeds 1%, the strength will be too high and the fr and p will be too high, leading to a decrease in low temperature toughness and increasing the cost, so the content should be set at 0.1-1.0%. Preferably '0.2
It is 5-0.6%.
ＮｂはＭｏと共存して焼戻し時の析出硬化に有用である
と共に、低Ｎ化と併せてＢの焼入性向上を可能とするが
０．００５％未満では効果がない。また００５チを超え
るとコストが高くなると共に溶接性を損うため０．００
５〜０．０５％とする。望ましくは０、Ｏ１〜０．０２
５％が良い。Nb coexists with Mo and is useful for precipitation hardening during tempering, and also makes it possible to improve the hardenability of B in combination with a low N content, but it is ineffective if it is less than 0.005%. In addition, if it exceeds 0.05, the cost will increase and weldability will be impaired, so 0.00
5 to 0.05%. Preferably 0, O1-0.02
5% is good.
Ａｔは鋼の脱酸のために添加されるが、０．１チを超え
ると鋼の清浄性を阻害するため０．１％を上限とする。At is added to deoxidize the steel, but if it exceeds 0.1%, it impedes the cleanliness of the steel, so the upper limit is set at 0.1%.
Ｂは一般に焼入性を高めるのに有用であるが、特に本発
明鋼ではＮｂ添加、低Ｎ化およびＭｏ添加の複合効果に
よシ著しい焼入性の向上が可能であるが、多量に添加す
ると溶接性を阻害するので上限は０．０１チとする。B is generally useful for improving hardenability, and in particular in the steel of the present invention, it is possible to significantly improve hardenability due to the combined effects of Nb addition, low N content, and Mo addition. This impedes weldability, so the upper limit is set to 0.01 inch.
Ｎは一般に不可避元素であると共に、Ｂの焼入性を阻害
する元素であるが、少量のＮｂで焼入性向上をはかるこ
とが可能な上限は０．０Ｏｎである。Although N is generally an unavoidable element and an element that inhibits the hardenability of B, the upper limit at which the hardenability can be improved with a small amount of Nb is 0.0 On.
望ましくは０１００４％以下が良い。Desirably, it is 01004% or less.
Ｃｒは焼入性向上に有用であるが、多量に添加すると溶
接性を阻害するので上限を１．０チとする。Cr is useful for improving hardenability, but if added in large amounts it impedes weldability, so the upper limit is set at 1.0.
Ｎｉは焼入性向上に有用であるが多いと高価になるので
上限を１．０％とする。Ni is useful for improving hardenability, but if too much Ni becomes expensive, the upper limit is set at 1.0%.
Ｃｕは鋼の焼入性を高め強度上昇に有用であるが、添加
量が多いと鋼板表面割れを生じやすくさせると共に高価
になるので１−以下とする。Cu is useful for improving the hardenability of steel and increasing its strength, but if added in a large amount, it makes the steel sheet surface more likely to crack and becomes expensive, so it is set at 1- or less.
Ｃ＆は製鋼時に添加して鋼の脱酸を良好にし、介在物の
減少、硫化物系介在物の形態制御を行なって低温靭性を
向上させるのに有用であるが鋼中に多量に存在すると有
嚇な非金属介在物を生成し、逆に低温靭性を阻害するた
め０．０１チ以下とする。C& is useful when added during steelmaking to improve the deoxidation of steel, reduce inclusions, control the morphology of sulfide inclusions, and improve low-temperature toughness. The thickness is set to 0.01 inch or less because it produces threatening nonmetallic inclusions and impairs low-temperature toughness.
次に不純物として不可避的に含有するＰ、Ｓについては
特に限定するものではないが、鋼の清浄性全通じて材質
を安定化するため少い程よく、このような観点からＰは
０．０２０％以下、Ｓは０．０１０−以下とすることが
望ましい。Next, P and S, which are unavoidably contained as impurities, are not particularly limited, but in order to stabilize the material throughout the cleanliness of the steel, the less the better, from this point of view P should be 0.020%. Hereinafter, it is desirable that S be 0.010- or less.
次に前記組成を有する鋼の加熱−圧延−熱処理条件の限
定理由について述べる。Next, the reasons for limiting the heating-rolling-heat treatment conditions for steel having the above composition will be described.
加熱温度はＮｉ）が固溶する温度として１０００℃以上
必要である。圧延終了温度は低くなると焼入れ性が吐下
し、その結釆・焼戻し後の低温靭性が劣化するため８０
０℃以上とする。The heating temperature is required to be 1000° C. or higher to form a solid solution of Ni. As the rolling end temperature becomes lower, the hardenability decreases, and the low-temperature toughness after consolidation and tempering deteriorates.
The temperature shall be 0°C or higher.
次いで圧延後直ちに急冷を行うが冷却開始温度が低くな
ると焼入れ性が低下するので８００℃以上からの急冷が
好ましい。この急冷はオンライン上で水、ミスト等の冷
却媒体を鋼板の表裏面に供給して行うものである。急冷
後の温度は高いと完全な焼入れ組織とすることかむずか
しいため２００℃を上限とする。Next, immediately after rolling, quenching is performed, but if the cooling start temperature becomes low, hardenability decreases, so quenching from 800° C. or higher is preferable. This rapid cooling is performed online by supplying a cooling medium such as water or mist to the front and back surfaces of the steel plate. If the temperature after quenching is high, it is difficult to obtain a completely hardened structure, so the upper limit is set at 200°C.
前記処理を経た後、焼戻し熱処理を施すものであるがフ
ェライト域で１暁戻すことが良好な低温靭性を得るのに
不可欠であるため上限温度をＡｃ＋／ａ度とする。After the above-mentioned treatment, a tempering heat treatment is performed, and since it is indispensable to return the steel for one hour in the ferrite region to obtain good low-temperature toughness, the upper limit temperature is set to Ac+/a degrees.
（実施例） 次に実施例を比較例と共に挙げる。(Example) Next, examples will be listed together with comparative examples.
第１表に示す化学成分を有する鋼を用いて第２表に示す
加熱−圧延−熱処理を施した。゛得られた鋼板の機械的
性質と溶接割れ性を併せて第２表に示す。Steel having the chemical composition shown in Table 1 was subjected to heating-rolling-heat treatment shown in Table 2. Table 2 shows the mechanical properties and weld cracking resistance of the obtained steel plate.
＝１８３
第２表から明らかなように、本発明実施例の場合にはい
ずれも８０ ｋｌ？ｆ／ａ＋２以上の高強度に加え、２
５頭板厚では一６０℃以上板厚５５＋ａ＋では一５０℃
以上の高靭性を示し、かつ溶接割れ性の一つの判定基準
であるＹ割れ停止温度が室温と極めて良好な溶接割れ性
を備えた使用者にとって使いやすい厚鋼板を製造できた
。就中、例Ｃ，Ｄ、ＥはＣｕ ＋ Ｃｒ １ ｖ ＊
ｃａのうち１種又は２種以上の合金元素を含む例である
。=183 As is clear from Table 2, in all cases of the embodiments of the present invention, 80 kl? In addition to high strength of f/a+2 or more,
5-head plate thickness -60℃ or higher plate thickness 55+a+ -50℃
It was possible to manufacture a thick steel plate that is easy for users to use, exhibiting the above-mentioned high toughness, and having an extremely good weld cracking resistance with a Y crack stop temperature of room temperature, which is one criterion for weld cracking resistance. In particular, Examples C, D, and E are Cu + Cr 1 v *
This is an example containing one or more alloying elements among ca.
例Ｆ、Ｇ、Ｈは比較例である。例ＦはＢを含まずＤＱＴ
処理をじたものであるが、８０キロ鋼の強度としてやや
不足し且つ低温靭性も低い。Examples F, G, and H are comparative examples. Example F does not include B and is DQT
Although it is similar to the treatment, it is slightly lacking in strength of 80kg steel and has low low temperature toughness.
例ＧはＮｆｉが高い例であるが、やはり強度が低く且つ
、低温靭性も低い。Example G has a high Nfi, but also has low strength and low temperature toughness.
例ＨはＣ含有量が高い例で、これを従来のオフライン焼
入れ焼戻しした例である。強度・靭性ともほぼ良好であ
るがＹ割れ停止温度が１２５℃となって溶接割れ性が劣
る。Example H is an example with a high C content, and is an example of conventional off-line quenching and tempering. Although the strength and toughness are almost good, the Y crack stop temperature is 125°C, and the weld cracking resistance is poor.
（発明の効果）
以上のとおシ、本発明はＮｂ −Ｍｅ −Ｂ−低Ｎ鋼を
用い加熱−圧延−オンライン焼入れ−１尭戻しのプロセ
スとし、特に加熱時の固溶Ｎｂ、 Ｍｏ （ｉり有効析
出を最大限に活用すると共に、低ＮとＩｖＩｏ 、 Ｎ
ｂの復合添＞ＪｌｌによりＢの：１’Ａ人性改善を徹底
し、すぐれた焼入性を付与したもので、成分的に従来の
８０キロ級鋼に多く添加されていたＮｉを大幅に省略し
かつわずかなＮｂ 、 Ｍｏ等の合金添加全行ない熱処
理についてもオフライン焼入れ熱処理が省略できるため
高靭性、高強度ｙ１４を極めて安価に製造できるという
効果がある。(Effects of the Invention) As described above, the present invention uses a Nb-Me-B-low N steel and uses a heating-rolling-on-line quenching-1-returning process. Maximizes effective precipitation while providing low N and IvIo, N
Recombinant addition of B> Jll has thoroughly improved the properties of B:1'A, giving it excellent hardenability, and has largely omitted Ni, which was added in large amounts to conventional 80 kg class steel. In addition, even in the case of heat treatment in which only a small amount of alloys such as Nb and Mo are added, offline quenching heat treatment can be omitted, resulting in the effect that high toughness and high strength Y14 can be manufactured at extremely low cost.
手続補正書（自発）
昭和６０年７月２ 日
特許庁長官 志 賀 学 殿
■、事件の表示
昭和５９年特許願ｆ！ １２４４４２号２、発明の名称
溶接性にすぐれた高強度鋼の製造方法
３、補正をする者
事件との関係 特許出願人
代表者 武 １） 豊
６ 補正の対象
（すＩすＪ １１＋１ 、ｌ”ｉｆ ７頁１３行と１４
行の間に下記文章を挿入する。。Procedural amendment (voluntary) July 2, 1985 Mr. Manabu Shiga, Director General of the Patent Office ■, Indication of the case 1988 Patent application f! 124442 No. 2, Name of the invention Method for manufacturing high-strength steel with excellent weldability 3, Relationship with the case of the person making the amendment Patent applicant representative Takeshi 1) Yutaka 6 Subject of amendment (SuIsu J 11+1, l” if page 7 lines 13 and 14
Insert the following text between the lines. .
［■は鋼を強化する。しかし多量に添加すると溶接性を
損なうので０，１％以下とする。Ｊ（２１同］０頁７Ｐ
、１表中、本発明Ｅのその他の榴［Ｃｒ Ｏ，３Ｖ ０
．０’３ Ｃａ Ｏ，００３６Ｊを［ｃｒｏ、３Ｖ
Ｏ，０３Ｃａ Ｏ，００３６Ｎｉ Ｏ，２Ｊに補正する
。[■ strengthens steel. However, if added in a large amount, weldability will be impaired, so the content should be 0.1% or less. J (21) 0 pages 7 pages
, In Table 1, other metals of the present invention E [Cr O, 3V 0
．． 0'3 Ca O, 0036J [cro, 3V
Corrected to O,03Ca O,0036Ni O,2J.
（３）同１２頁８行１” Ｃｕ ＋ Ｃｒ ＋ Ｖ ＊
Ｃａ Ｊをｒ Ｃｕ ＋ Ｎｉ ＊Ｃｒ、 Ｖ、 Ｃ
ａ ｊに補正する。(3) Same page 12, line 8 1” Cu + Cr + V *
Ca J r Cu + Ni *Cr, V, C
Correct to a j.
Claims (1)
以下、Ｍｎ：０．５０〜２．００％、Ｍｏ：０．１０〜
１．０％、Ｎｂ：０．００５〜０．０５％、Ｂ：０．０
１％以下、Ａｌ：０．１％以下、Ｎ：０．００６０％以
下、を基本成分とし、必要に応じて Ｃｒ：１％以下、Ｎｉ：１％以下、 Ｃｕ：１％以下、Ｖ：０．１％以下、 Ｃａ：０．０１％以下のうち１種または２種以上を含有
し、残部Ｆｅおよび不可避不純物よりなる鋼を、加熱温
度１０００℃以上、圧延終了温度８００℃以上の条件で
加熱圧延し、圧延後直ちに２００℃以下まで急冷した後
、Ａｃ＿１点以下で焼戻し熱処理を施こすことを特徴と
する溶接性にすぐれた高強度鋼の製造方法。[Claims] C: 0.04-0.11%, Si: 1.0% in weight%
Below, Mn: 0.50~2.00%, Mo: 0.10~
1.0%, Nb: 0.005-0.05%, B: 0.0
The basic components are 1% or less, Al: 0.1% or less, N: 0.0060% or less, and if necessary, Cr: 1% or less, Ni: 1% or less, Cu: 1% or less, V: 0. .1% or less, Ca: 0.01% or less, and the balance consists of Fe and unavoidable impurities, and the steel is heated at a heating temperature of 1000°C or higher and a rolling end temperature of 800°C or higher. A method for producing high-strength steel with excellent weldability, which comprises rolling, quenching immediately after rolling to 200°C or lower, and then subjecting it to tempering heat treatment at a temperature of Ac_1 or lower.
Priority Applications (6)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12444284A JPH0227407B2 (en) | 1984-06-19 | 1984-06-19 | YOSETSUSEINISUGURETAKOKYODOKONOSEIZOHOHO |
| EP85304223A EP0165774B2 (en) | 1984-06-19 | 1985-06-13 | Method for producing high-strength steel having improved weldability |
| DE8585304223T DE3579376D1 (en) | 1984-06-19 | 1985-06-13 | METHOD FOR PRODUCING HIGH-STRENGTH STEEL WITH WELDABILITY. |
| CA000484073A CA1246969A (en) | 1984-06-19 | 1985-06-14 | Method for producing high-strength steel having improved weldability |
| AU43772/85A AU558845B2 (en) | 1984-06-19 | 1985-06-18 | High strength, weldable, low alloy steel |
| US07/453,141 US4988393A (en) | 1984-06-19 | 1989-12-12 | Method for producing high-strength steel having improved weldability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12444284A JPH0227407B2 (en) | 1984-06-19 | 1984-06-19 | YOSETSUSEINISUGURETAKOKYODOKONOSEIZOHOHO |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS613833A true JPS613833A (en) | 1986-01-09 |
| JPH0227407B2 JPH0227407B2 (en) | 1990-06-18 |
Family
ID=14885602
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP12444284A Expired - Lifetime JPH0227407B2 (en) | 1984-06-19 | 1984-06-19 | YOSETSUSEINISUGURETAKOKYODOKONOSEIZOHOHO |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0227407B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61166918A (en) * | 1985-01-17 | 1986-07-28 | Nippon Steel Corp | Manufacture of steel with sulfide stress corrosion cracking resistance |
| JPS61186453A (en) * | 1985-02-13 | 1986-08-20 | Kobe Steel Ltd | High strength and high toughness quenched and tempered low-carbon steel plate for boiler or pressure vessel having superior resistance to weld crack, erosion and creep |
| JPS61250152A (en) * | 1985-04-26 | 1986-11-07 | Kobe Steel Ltd | Normalized low-carbon steel plate for boiler or pressure vessel having high strength and toughness |
| JPS62146247A (en) * | 1985-12-20 | 1987-06-30 | Kobe Steel Ltd | Cr-mo steel plate for multilayer vessel |
| JPS63145711A (en) * | 1986-12-08 | 1988-06-17 | Kobe Steel Ltd | Production of high tension steel plate having excellent low temperature toughness |
| JPH0375310A (en) * | 1989-08-15 | 1991-03-29 | Kobe Steel Ltd | Production of heat treated high tensile strength steel plate excellent in weldability and brittle fracture propagation arresting property |
-
1984
- 1984-06-19 JP JP12444284A patent/JPH0227407B2/en not_active Expired - Lifetime
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61166918A (en) * | 1985-01-17 | 1986-07-28 | Nippon Steel Corp | Manufacture of steel with sulfide stress corrosion cracking resistance |
| JPS61186453A (en) * | 1985-02-13 | 1986-08-20 | Kobe Steel Ltd | High strength and high toughness quenched and tempered low-carbon steel plate for boiler or pressure vessel having superior resistance to weld crack, erosion and creep |
| JPS61250152A (en) * | 1985-04-26 | 1986-11-07 | Kobe Steel Ltd | Normalized low-carbon steel plate for boiler or pressure vessel having high strength and toughness |
| JPS62146247A (en) * | 1985-12-20 | 1987-06-30 | Kobe Steel Ltd | Cr-mo steel plate for multilayer vessel |
| JPS63145711A (en) * | 1986-12-08 | 1988-06-17 | Kobe Steel Ltd | Production of high tension steel plate having excellent low temperature toughness |
| JPH0375310A (en) * | 1989-08-15 | 1991-03-29 | Kobe Steel Ltd | Production of heat treated high tensile strength steel plate excellent in weldability and brittle fracture propagation arresting property |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0227407B2 (en) | 1990-06-18 |
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