JP2019019382A - Low alloy steel - Google Patents
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本発明は、低合金鋼に関する。 The present invention relates to a low alloy steel.
薄鋼板、厚鋼板、鋼管、棒線などの種々の分野で、高強度化ならびに使用環境の過酷化に伴い、水素脆化が問題となっている。水素脆化が問題となる用途としては、例えば、自動車用の高強度薄鋼板、建材用の厚鋼板、油井管やラインパイプ等の過酷環境で使われる鋼管、高強度の棒線・棒鋼・ボルトなどが挙げられる。 In various fields such as thin steel plates, thick steel plates, steel pipes and rods, hydrogen embrittlement has become a problem as the strength increases and the usage environment becomes severe. Applications in which hydrogen embrittlement is a problem include, for example, high-strength steel sheets for automobiles, thick steel sheets for building materials, steel pipes used in harsh environments such as oil well pipes and line pipes, and high-strength bars, bars and bolts. Etc.
ｂｃｃ構造を有する炭素鋼や低合金鋼の耐水素脆化特性を改善する組織上の対策としては、例えばマルテンサイト系の材料では、焼戻し温度を高めることによる粒界炭化物の球状化や、水素トラップ効果を有する微細な合金炭化物の活用が知られている（非特許文献１および非特許文献２）。 As structural measures to improve the hydrogen embrittlement resistance of carbon steel and low alloy steel having a bcc structure, for example, in martensitic materials, spheroidization of grain boundary carbides by increasing the tempering temperature, hydrogen trap Utilization of fine alloy carbide having an effect is known (Non-Patent Document 1 and Non-Patent Document 2).
上記の対策は、焼戻し時に生じる炭化物の作用に着目し、これを制御するものである。一方、Ｆｅ以外の合金元素を添加した場合には、その一部がｂｃｃ構造の母相中に固溶し、この固溶元素を活用すれば、熱処理に依存しなくても普遍的な耐水素脆化特性が得られることが期待される。 The above measures pay attention to the action of carbides generated during tempering and control this. On the other hand, when an alloy element other than Fe is added, a part of it is dissolved in the matrix phase of the bcc structure, and if this solid solution element is used, universal hydrogen resistance can be achieved without depending on heat treatment. It is expected that embrittlement characteristics can be obtained.
ただし、Ｆｅ以外の固溶合金元素は一般には水素拡散係数を低下させ、使用環境中における吸蔵水素濃度を増加させ、水素脆化に対して悪影響を及ぼすと考えられている（非特許文献３および非特許文献４）。 However, solid solution alloy elements other than Fe are generally considered to have a negative effect on hydrogen embrittlement by lowering the hydrogen diffusion coefficient and increasing the concentration of occluded hydrogen in the use environment (Non-patent Documents 3 and 3). Non-patent document 4).
特許文献１には、固溶窒素量を０．００４〜０．０３質量％に制限した冷間加工用鋼材に関する発明が開示されている。この冷間加工用鋼材によれば、冷間加工のみで高強度が得られるため、熱処理を省略することができる、としている。 Patent Document 1 discloses an invention relating to a steel material for cold working in which the amount of dissolved nitrogen is limited to 0.004 to 0.03% by mass. According to this steel material for cold work, since high strength can be obtained only by cold work, heat treatment can be omitted.
本発明者らは、純鉄系の材料を用いて、各種の合金元素を完全に固溶させた合金を用いて鋭意検討を行った結果、主として、ＳｉおよびＡｌは、固溶状態でも水素拡散係数を低下させず、かつ耐水素脆化特性の改善効果を有することを見出した。上記改善効果の作用機構については、詳細は不明であるが、これらの元素は表面エネルギーを高めて腐食環境における水素侵入を抑制する効果がある。水素侵入の抑制機構は、金属表面に水素原子が吸着した状態を不安定化させ、水素分子に速やかに再結合させ、系外に逃散させることと推定されている。この効果と同様に、鉄中にＳｉおよびＡｌが固溶している場合、鉄中を拡散して近づいて来た水素原子を反発し、拡散を促進することで水素原子が脆化起点(応力集中部や介在物などの界面)に集積するのを防止し、水素脆化を抑制すると推定される。 As a result of intensive studies using an alloy in which various alloying elements are completely dissolved in a pure iron-based material, the present inventors mainly conducted hydrogen diffusion even in a solid solution state. It has been found that the coefficient is not lowered and the hydrogen embrittlement resistance is improved. Although the details of the action mechanism of the improvement effect are unknown, these elements have the effect of increasing the surface energy and suppressing hydrogen intrusion in a corrosive environment. The suppression mechanism of hydrogen intrusion is presumed to destabilize the state in which hydrogen atoms are adsorbed on the metal surface, quickly recombine with hydrogen molecules, and escape from the system. Similar to this effect, when Si and Al are dissolved in iron, the hydrogen atoms that diffused in the iron are repelled and promoted to promote the diffusion, thereby causing the hydrogen atoms to start from embrittlement (stress It is presumed that accumulation at the interface of concentrated portions and inclusions is prevented and hydrogen embrittlement is suppressed.
特許文献１の発明は、Ｓｉ、Ａｌの固溶量を確保することによる耐水素脆化特性について全く考慮されていない。また、調質のための熱処理、いわゆる焼入れ／焼戻し熱処理を省略することを前提としているが、熱処理を省略したこのような非調質鋼の場合、製造工程中の徐冷過程でＳｉやＡｌが析出するため、この技術では、Ｓｉ、Ａｌの固溶量を確保することはできない。 In the invention of Patent Document 1, no consideration is given to the hydrogen embrittlement resistance by ensuring the solid solution amount of Si and Al. In addition, it is assumed that heat treatment for tempering, so-called quenching / tempering heat treatment, is omitted, but in the case of such non-tempered steel in which heat treatment is omitted, Si and Al are contained in the slow cooling process during the manufacturing process. Since it precipitates, this technique cannot secure the solid solution amount of Si and Al.
本発明は、ＳｉおよびＡｌを固溶状態で存在させることにより耐水素脆化特性の改善させた低合金鋼を提供することを目的とする。 An object of the present invention is to provide a low alloy steel having improved hydrogen embrittlement resistance by allowing Si and Al to exist in a solid solution state.
本発明は、下記の低合金鋼を要旨とする。 The gist of the present invention is the following low alloy steel.
〔１〕質量％で、
Ｃ：０．０１％以下と、
Ｓｉ：０．０５〜１０．０％およびＡｌ：０．０１〜１０．０％の両方またはいずれか一方と、
Ｐ：０．０２５％以下、
Ｓ：０．０１０％以下、
Ｏ：０．００５％以下、
Ｎ：０．００８％以下、
Ｍｎ：０〜１．０％、
Ｂ：０〜０．００３％、
Ｃｒ：０〜５．０％、
Ｍｏ：０〜５．０％、
Ｖ：０〜５．０％、
Ｗ：０〜５．０％、
Ｎｂ：０〜０．１％、
Ｔｉ：０〜０．１％、
Ｚｒ：０〜０．２％、
Ｈｆ：０〜０．２％、
Ｔａ：０〜０．２％、
Ｃｕ：０〜３．０％、
Ｎｉ：０〜５．０％、
Ｃｏ：０〜３．０％、
Ｃａ：０〜０．０１％、
Ｍｇ：０〜０．０１％、
ＲＥＭ：０〜０．５０％と、
残部：Ｆｅおよび不純物とである化学組成を有し、
下記（１）式から求められるＦｎ１が１．０〜１０．０であり、
下記（２）式から求められるＦｎ２が１．０〜１０．０である、
耐水素脆化特性に優れる低合金鋼。
Ｆｎ１ ＝ Ｓｉ＋Ａｌ （質量％）（１）
Ｆｎ２ ＝ Ｓｉ＋Ａｌ （固溶分の質量％）（２）
ただし、（１）式中の各元素記号は、低合金鋼中に含まれる各元素の含有量（質量％）を意味し、（２）式中の各元素記号は、低合金鋼中に固溶状態で存在する各元素の含有量（質量％）を意味する。
[1] By mass%
C: 0.01% or less,
Si: 0.05 to 10.0% and Al: 0.01 to 10.0% or either one of them,
P: 0.025% or less,
S: 0.010% or less,
O: 0.005% or less,
N: 0.008% or less,
Mn: 0 to 1.0%,
B: 0 to 0.003%,
Cr: 0 to 5.0%,
Mo: 0 to 5.0%,
V: 0 to 5.0%,
W: 0 to 5.0%,
Nb: 0 to 0.1%,
Ti: 0 to 0.1%,
Zr: 0 to 0.2%,
Hf: 0 to 0.2%,
Ta: 0 to 0.2%,
Cu: 0 to 3.0%,
Ni: 0 to 5.0%,
Co: 0 to 3.0%,
Ca: 0 to 0.01%,
Mg: 0 to 0.01%,
REM: 0 to 0.50%,
The balance: having a chemical composition that is Fe and impurities,
Fn1 calculated | required from the following (1) Formula is 1.0-10.0,
Fn2 calculated | required from following (2) Formula is 1.0-10.0,
Low alloy steel with excellent hydrogen embrittlement resistance.
Fn1 = Si + Al (mass%) (1)
Fn2 = Si + Al (mass% of solid solution content) (2)
However, each element symbol in the formula (1) means the content (mass%) of each element contained in the low alloy steel, and each element symbol in the formula (2) is solid in the low alloy steel. It means content (mass%) of each element which exists in a solution state.
〔２〕質量％で、
Ｍｎ：０．１〜１．０％、
Ｂ：０．０００３〜０．００３％
Ｃｒ：０．０１〜５．０％、
Ｍｏ：０．０１〜５．０％、
Ｖ：０．０１〜５．０％、
Ｗ：０．０１〜５．０％、
Ｎｂ：０．００１〜０．１％、
Ｔｉ：０．００１〜０．１％、
Ｚｒ：０．００１〜０．２％、
Ｈｆ：０．００１〜０．２％、
Ｔａ：０．００１〜０．２％、
Ｃｕ：０．１〜３．０％、
Ｎｉ：０．１〜５．０％、
Ｃｏ：０．１〜３．０％、
Ｃａ：０．０００１〜０．０１％、
Ｍｇ：０．０００１〜０．０１％および
ＲＥＭ：０．０００１〜０．５０％から選択される一種以上を含有する、
上記〔１〕の低合金鋼。
[2] In mass%,
Mn: 0.1 to 1.0%,
B: 0.0003 to 0.003%
Cr: 0.01 to 5.0%,
Mo: 0.01 to 5.0%,
V: 0.01-5.0%,
W: 0.01-5.0%,
Nb: 0.001 to 0.1%,
Ti: 0.001 to 0.1%,
Zr: 0.001 to 0.2%,
Hf: 0.001 to 0.2%,
Ta: 0.001 to 0.2%,
Cu: 0.1 to 3.0%,
Ni: 0.1 to 5.0%,
Co: 0.1-3.0%
Ca: 0.0001 to 0.01%,
One or more selected from Mg: 0.0001 to 0.01% and REM: 0.0001 to 0.50%,
The low alloy steel of [1] above.
〔３〕析出物、介在物および金属間化合物の合計量が０．５質量％以下である、
上記〔１〕または〔２〕の低合金鋼。
[3] The total amount of precipitates, inclusions and intermetallic compounds is 0.5% by mass or less.
The low alloy steel according to the above [1] or [2].
本発明によれば、耐水素脆化特性に優れた低合金鋼が得られる。 According to the present invention, a low alloy steel excellent in hydrogen embrittlement resistance can be obtained.
１．化学組成
本発明に係る低合金鋼は、下記の化学組成を有する。各元素の含有量の範囲および限定理由を説明する。各元素の含有量の％は、「質量％」を意味する。
1. Chemical Composition The low alloy steel according to the present invention has the following chemical composition. The range of the content of each element and the reason for limitation will be described. % Of the content of each element means “mass%”.
Ｃ：０．０１％以下
Ｃは、固溶強化により鋼の強度を高めるのに有効であるが、０．０１％を超えて含有させると、母相のフェライト地に固溶しきれなくなり、焼鈍時に粗大な炭化物を形成し、耐水素脆化特性を低下させる。この観点から、Ｃの含有量は０．０１％以下とする。Ｃ含有量は、低ければ低いほど望ましい。
C: 0.01% or less C is effective in increasing the strength of the steel by solid solution strengthening. However, if it exceeds 0.01%, it cannot be completely dissolved in the ferrite phase of the parent phase and is annealed. Sometimes coarse carbides are formed and the hydrogen embrittlement resistance is reduced. From this viewpoint, the C content is 0.01% or less. The lower the C content, the better.
Ｓｉ：０．０５〜１０．０％および
Ａｌ：０．０１〜１０．０％の両方またはいずれか一方
ＳｉおよびＡｌは、鋼の脱酸に有効な元素であるが、本発明においては、耐水素脆化特性を向上させるために重要な元素である。脱酸の効果を得る観点ではＳｉは０．０５％以上、Ａｌは０．０１％以上含有させれば十分であるが、優れた耐水素脆化特性を得るためには、ＳｉおよびＡｌの合計含有量を１．０％以上とする必要がある。一方、耐水素脆化特性の効果は、過剰に含有させても飽和するので、それぞれの元素の含有量の上限および合計含有量の上限は１０．０％とする。すなわち、下記（１）式から求められるＦｎ１が１．０〜１０．０であることが必要である。一方、耐水素脆化特性は、特に、鋼中に固溶したＳｉおよびＡｌによって得られるので、下記（２）式から求められるＦｎ２が１．０〜１０．０であることも必要である。
Ｆｎ１ ＝ Ｓｉ＋Ａｌ （質量％）（１）
Ｆｎ２ ＝ Ｓｉ＋Ａｌ （固溶分の質量％）（２）
ただし、（１）式中の各元素記号は、低合金鋼中に含まれる各元素の含有量（質量％）を意味し、（２）式中の各元素記号は、低合金鋼中に固溶状態で存在する各元素の含有量（質量％）を意味する。
Si: 0.05-10.0% and Al: 0.01-10.0% and / or either Si and Al are effective elements for deoxidation of steel. It is an important element for improving hydrogen embrittlement characteristics. In order to obtain the effect of deoxidation, it is sufficient to contain Si by 0.05% or more and Al by 0.01% or more. In order to obtain excellent hydrogen embrittlement resistance, the total of Si and Al is sufficient. The content needs to be 1.0% or more. On the other hand, since the effect of hydrogen embrittlement resistance is saturated even if it is excessively contained, the upper limit of the content of each element and the upper limit of the total content are set to 10.0%. That is, Fn1 calculated | required from the following (1) formula needs to be 1.0-10.0. On the other hand, since the hydrogen embrittlement resistance is obtained particularly by Si and Al dissolved in steel, it is also necessary that Fn2 obtained from the following formula (2) is 1.0 to 10.0.
Fn1 = Si + Al (mass%) (1)
Fn2 = Si + Al (mass% of solid solution content) (2)
However, each element symbol in the formula (1) means the content (mass%) of each element contained in the low alloy steel, and each element symbol in the formula (2) is solid in the low alloy steel. It means content (mass%) of each element which exists in a solution state.
耐水素脆化特性を向上させるためには、Ｆｎ１の下限を１．５とするのが好ましく、２．０とするのがより好ましく、Ｆｎ２の下限も１．５とするのが好ましく、２．０とするのがより好ましい。一方、Ｓｉ、Ａｌのいずれも過剰に含有させてもその効果は小さくなるため、Ｆｎ１の上限を７．０とするのが好ましく、５．０とするのがより好ましく、Ｆｎ２の上限も７．０とするのが好ましく、５．０とするのがより好ましい。 In order to improve hydrogen embrittlement resistance, the lower limit of Fn1 is preferably 1.5, more preferably 2.0, and the lower limit of Fn2 is also preferably 1.5. More preferably 0. On the other hand, since the effect becomes small even if both Si and Al are contained excessively, the upper limit of Fn1 is preferably 7.0, more preferably 5.0, and the upper limit of Fn2 is also 7. It is preferably 0, and more preferably 5.0.
Ｐ：０．０２５％以下
Ｐは、鋼中に不純物として存在する元素である。Ｐは、粒界に偏析し、耐水素脆化特性を低下させる元素であるため、その含有量は０．０２５％以下とする必要がある。Ｐの含有量はできるだけ少ない方が望ましい。
P: 0.025% or less P is an element present as an impurity in steel. P is an element that segregates at the grain boundaries and reduces the resistance to hydrogen embrittlement, and therefore its content needs to be 0.025% or less. The content of P is preferably as low as possible.
Ｓ：０．０１０％以下
Ｓは、鋼中に不純物として存在する元素である。ＳもＰと同様に粒界に偏析し，耐水素脆化特性を低下させる元素であるため、その含有量は０．０１％以下とする必要がある。Ｓの含有量はできるだけ少ない方が望ましい。
S: 0.010% or less S is an element present as an impurity in steel. Similarly to P, S is an element that segregates at the grain boundary and reduces the resistance to hydrogen embrittlement, so its content must be 0.01% or less. The content of S is preferably as low as possible.
Ｏ：０．００５％以下
Ｏ（酸素）は，鋼中に不純物として存在する元素である。その含有量が０．００５％を超えると、粗大な酸化物を形成し、靭性等の機械的特性を低下させる。従って、Ｏ（酸素）は０．００５％以下とする。Ｏ（酸素）の含有量はできるだけ低い方が望ましい。その上限は望ましくは０．００４％、さらに望ましくは０．００３％である。
O: 0.005% or less O (oxygen) is an element present as an impurity in steel. When the content exceeds 0.005%, a coarse oxide is formed, and mechanical properties such as toughness are lowered. Therefore, O (oxygen) is made 0.005% or less. The content of O (oxygen) is preferably as low as possible. The upper limit is desirably 0.004%, and more desirably 0.003%.
Ｎ：０．００８％以下
Ｎ（窒素）は、鋼中に不純物として存在する元素である。その含有量が０．００８％を超えると、粗大な窒化物を形成し、靭性等の機械的特性を低下させる。従って、Ｎ（窒素）は０．００８％以下とする。Ｎ（窒素）の含有量はできるだけ低い方が望ましい。その上限は望ましくは０．００６％、さらに望ましくは０．００５％である。
N: 0.008% or less N (nitrogen) is an element present as an impurity in steel. When the content exceeds 0.008%, coarse nitrides are formed, and mechanical properties such as toughness are lowered. Therefore, N (nitrogen) is 0.008% or less. The content of N (nitrogen) is preferably as low as possible. The upper limit is desirably 0.006%, and more desirably 0.005%.
Ｍｎ：０〜１．０％
Ｍｎは、固溶強化の効果を有するので、含有させてもよい。ただし、過剰に含有させても効果が飽和するので、含有させる場合の上限を１．０％とする。上記の効果を得るためには、０．１％以上含有させるのが好ましい。
Mn: 0 to 1.0%
Since Mn has an effect of solid solution strengthening, Mn may be contained. However, since an effect is saturated even if it makes it contain excessively, the upper limit in the case of making it contain shall be 1.0%. In order to acquire said effect, it is preferable to make it contain 0.1% or more.
Ｂ：０〜０．００３％
Ｂは、Ｃと同様に鋼の強度を高めるのに有効であるので、含有させてもよい。ただし、０．００３％を超えて含有させてもその効果は飽和するため、含有させる場合の上限を０．００３％とする。上記の効果を得るためには、０．０００３％以上含有させるのが好ましい。
B: 0 to 0.003%
Since B is effective in increasing the strength of steel in the same manner as C, it may be contained. However, since the effect is saturated even if it contains exceeding 0.003%, the upper limit in the case of making it contain shall be 0.003%. In order to acquire said effect, it is preferable to make it contain 0.0003% or more.
Ｃｒ：０〜５．０％
Ｍｏ：０〜５．０％
Ｖ：０〜５．０％
Ｗ：０〜５．０％
Ｎｂ：０〜０．１％
Ｔｉ：０〜０．１％
Ｚｒ：０〜０．２％
Ｈｆ：０〜０．２％
Ｔａ：０〜０．２％
Ｃｒ、Ｍｏ、Ｖ、Ｗ、Ｎｂ、Ｔｉ、Ｚｒ、ＨｆおよびＴａ（以下、これらの元素を「第１群元素」ともいう。）は、フェライト生成元素であり、かつ固溶強化能を有する。また、Ｎｂ、Ｔｉ、Ｚｒ、ＨｆおよびＴａは、炭窒化物の生成能が強く、焼鈍時に微細な炭窒化物を形成し、固溶Ｃや固溶Ｎを低減する効果を有する。このため、これらの元素の一種以上を含有させてもよい。ただし、それぞれの元素の含有量が過剰な場合には効果が飽和するので、これらの元素を含有させる場合には、Ｃｒは５．０％以下、Ｍｏは５．０％以下、Ｖは５．０％以下、Ｗは５．０％以下、Ｎｂは０．１％以下、Ｔｉは０．１％以下、Ｚｒは０．２％以下、Ｈｆは０．２％以下、Ｔａは０．２％以下とする。また、上記の効果を得るためには、Ｃｒは０．０１％以上、Ｍｏは０．０１％以上、Ｖは０．０１％以上、Ｗは０．０１％以上、Ｎｂは０．００１％以上、Ｔｉは０．００１％以上、Ｚｒは０．００１％以上、Ｈｆは０．００１％以上、Ｔａは０．００１％以上含有させるのが好ましい。
Cr: 0 to 5.0%
Mo: 0 to 5.0%
V: 0 to 5.0%
W: 0 to 5.0%
Nb: 0 to 0.1%
Ti: 0 to 0.1%
Zr: 0 to 0.2%
Hf: 0 to 0.2%
Ta: 0 to 0.2%
Cr, Mo, V, W, Nb, Ti, Zr, Hf and Ta (hereinafter, these elements are also referred to as “first group elements”) are ferrite-forming elements and have a solid solution strengthening ability. Further, Nb, Ti, Zr, Hf and Ta have a strong ability to form carbonitrides and have the effect of forming fine carbonitrides during annealing and reducing solid solution C and solid solution N. For this reason, you may contain 1 or more types of these elements. However, when the content of each element is excessive, the effect is saturated. Therefore, when these elements are contained, Cr is 5.0% or less, Mo is 5.0% or less, and V is 5. 0% or less, W is 5.0% or less, Nb is 0.1% or less, Ti is 0.1% or less, Zr is 0.2% or less, Hf is 0.2% or less, Ta is 0.2% The following. In order to obtain the above effect, Cr is 0.01% or more, Mo is 0.01% or more, V is 0.01% or more, W is 0.01% or more, and Nb is 0.001% or more. , Ti is preferably 0.001% or more, Zr is 0.001% or more, Hf is 0.001% or more, and Ta is preferably 0.001% or more.
Ｃｕ：０〜３．０％
Ｎｉ：０〜５．０％
Ｃｏ：０〜３．０％
Ｃｕ、ＮｉおよびＣｏは、いずれも鋼の固溶強化に有効である。このため、これらの元素から選択される一種以上を含有させてもよい。ただし、過剰に含有させてもその効果は飽和するので、ＣｕおよびＣｏはその上限を３．０％とし、Ｎｉはその上限を５．０％とする。また、上記の効果を得るためには、いずれの元素も０．１％以上含有させるのが好ましい。
Cu: 0 to 3.0%
Ni: 0 to 5.0%
Co: 0 to 3.0%
Cu, Ni and Co are all effective for solid solution strengthening of steel. For this reason, you may contain 1 or more types selected from these elements. However, even if contained excessively, the effect is saturated, so the upper limit of Cu and Co is 3.0%, and the upper limit of Ni is 5.0%. Moreover, in order to acquire said effect, it is preferable to contain 0.1% or more of any element.
Ｃａ：０〜０．０１％
Ｍｇ：０〜０．０１％
ＲＥＭ：０〜０．５０％
Ｃａ、ＭｇおよびＲＥＭは、鋼中のＳと結合して硫化物を形成し、介在物の形状を改善して靭性等の機械的特性を改善するので、含有させてもよい。過剰に含有させてもこの効果は飽和するため、ＣａおよびＭｇの上限は、０．０１％、ＲＥＭの上限は０．５０％とする。上記の効果を得るためには、いずれの元素も０．０００１％以上含有させるのが好ましい。
Ca: 0 to 0.01%
Mg: 0 to 0.01%
REM: 0 to 0.50%
Ca, Mg, and REM combine with S in steel to form sulfides, improve the shape of inclusions and improve mechanical properties such as toughness, and therefore may be included. Since this effect is saturated even if contained excessively, the upper limit of Ca and Mg is 0.01%, and the upper limit of REM is 0.50%. In order to acquire said effect, it is preferable to contain 0.0001% or more of any element.
なお、ＲＥＭとは、Ｓｃ、Ｙ、およびランタノイドの合計１７元素を指し、「ＲＥＭの含有量」とは、ＲＥＭが１種の場合はその含有量、２種以上の場合はそれらの合計含有量を指す。また、ＲＥＭは一般的には複数種のＲＥＭの合金であるミッシュメタルとしても供給されている。このため、個別の元素を１種または２種以上添加してＲＥＭの量が上記の範囲となるように含有させてもよいし、例えば、ミッシュメタルの形で添加して、ＲＥＭの量が上記の範囲となるように含有させてもよい。 Note that REM refers to a total of 17 elements of Sc, Y, and lanthanoids, and “REM content” refers to the content when there is one REM, and the total content when there are two or more. Point to. REM is also supplied as misch metal, which is generally an alloy of a plurality of types of REM. For this reason, one or more individual elements may be added and contained so that the amount of REM is in the above range. For example, the amount of REM may be added in the form of misch metal. You may make it contain so that it may become this range.
本発明の化学組成は、上記の各元素をそれぞれ規定される範囲で含有し、残部は、Ｆｅおよび不純物である。不純物とは、鋼材を工業的に製造する際に、鉱石、スクラップ等の原料その他の要因により混入する成分を意味する。 The chemical composition of the present invention contains each of the above elements in a prescribed range, with the balance being Fe and impurities. An impurity means the component mixed by raw materials and other factors, such as an ore and a scrap, when manufacturing steel materials industrially.
２．金属組織
本発明鋼は、体積率で９９％以上がフェライトである、フェライト単相組織を対象とする。フェライト以外の組織については、特に制約がないが、水素脆化の起点および進展経路として働くので、その量はできるだけ少ないことが好ましい。このため、析出物、介在物および金属間化合物（以下、「析出物等」という。）の合計量は０．５質量％以下とするのが好ましい。
2. Metal structure The steel of the present invention is intended for a ferrite single-phase structure in which 99% or more of the volume is ferrite. There is no particular restriction on the structure other than ferrite, but it works as a starting point and a development path for hydrogen embrittlement, so the amount is preferably as small as possible. For this reason, the total amount of precipitates, inclusions and intermetallic compounds (hereinafter referred to as “precipitates”) is preferably 0.5% by mass or less.
３．製造方法
本発明鋼は、通常の方法で溶製（溶解および鋳造）し、熱間鍛造し、必要に応じてさらに熱間圧延することにより製造することができる。ただし、偏析を除去し、金属間化合物の生成を抑えるために、熱間鍛造後に１２００〜１３００℃で１時間以上保持のソーキング熱処理を行うのが望ましい。最終熱処理の焼鈍温度は、フェライトの単相組織が得られる条件であればよいが、通常は、７５０〜８５０℃の温度で、５分以上均熱し、その後に水冷するのがよい。析出物等の生成を低減するためには、単にＳｉおよびＡｌの含有量を調整するだけでは足りず、水冷工程の８００〜５００℃間の冷却速度を１０℃／ｓ以上するのがよい。必要に応じて、焼鈍後に冷間圧延等を施し、強度を高めてもよい。
3. Production Method The steel of the present invention can be produced by melting (melting and casting) by a normal method, hot forging, and further hot rolling as necessary. However, in order to remove segregation and suppress the formation of intermetallic compounds, it is desirable to perform a soaking heat treatment held at 1200 to 1300 ° C. for 1 hour or longer after hot forging. The annealing temperature of the final heat treatment may be any conditions as long as a single-phase structure of ferrite can be obtained, but it is usually preferable to soak at a temperature of 750 to 850 ° C. for 5 minutes or more and then cool with water. In order to reduce the formation of precipitates and the like, it is not sufficient to simply adjust the contents of Si and Al, and the cooling rate between 800 and 500 ° C. in the water cooling step should be 10 ° C./s or more. If necessary, cold rolling or the like may be performed after annealing to increase the strength.
本発明の効果を検証した実施例を以下に説明する。 Examples in which the effects of the present invention are verified will be described below.
表１に示す化学組成を有する低合金鋼をそれぞれ５０ｋｇ真空溶製した。得られた鋳片から、熱間鍛造、熱間圧延を経て、厚さ３０ｍｍの板材を得た後、８００℃で６０分加熱後水冷の焼鈍熱処理を行い、試験材（焼鈍材）を得た。また、焼鈍後に、減面率６０〜９４％の冷間圧延を施し、試験材（冷間圧延材）を得た。この際、引張強さが６００〜９００ＭＰａの範囲に入るように、素材に応じて冷間圧延率を調整した。 Each of the low alloy steels having chemical compositions shown in Table 1 was vacuum-melted by 50 kg. From the obtained slab, a plate material having a thickness of 30 mm was obtained through hot forging and hot rolling, and then heated at 800 ° C. for 60 minutes and then subjected to a water-cooled annealing heat treatment to obtain a test material (annealed material). . Moreover, after annealing, cold rolling with a reduction in area of 60 to 94% was performed to obtain a test material (cold rolled material). Under the present circumstances, the cold rolling rate was adjusted according to the raw material so that tensile strength might be in the range of 600-900 MPa.
＜析出物等の合計含有量の測定等＞
ＳｉおよびＡｌの合計固溶量、析出物等の合計含有量は、下記の手順により求めた。
試験材（焼鈍材）の中心部から、直径が１〜１０ｍｍで長さが５０ｍｍの寸法の抽出分析用丸棒試験片を採取した。この試験片を陽極電解してマトリックスを溶解させ、析出物等を抽出し、抽出された残渣を用いてＩＣＰ（高周波誘導結合プラズマ）発光分析を行い、残渣中のＳｉおよびＡｌの合計含有量を測定する。陽極電解は、１質量％の酒石酸を含む電解液を用いて定電流電解により行った。この合計含有量を、陽極電解によるマトリックス溶解前後での試験片の質量差（つまり、試験片の溶解量）で除して、マトリックス中に析出したＳｉおよびＡｌの合計含有量（質量％）を算出した。鋼材のＳｉおよびＡｌの合計含有量から、析出したＳｉおよびＡｌの合計含有量を差し引いて、固溶したＳｉおよびＡｌの合計含有量を計算した。また、マトリックスを溶解させ得られた残渣の合計量を、陽極電解によるマトリックス溶解前後での試験片の質量差（試験片の溶解量）で除して、析出物等の合計含有量（質量％）を求めた。
<Measurement of total content of precipitates, etc.>
The total content of Si and Al, the total content of precipitates and the like were determined by the following procedure.
A round bar specimen for extraction analysis having a diameter of 1 to 10 mm and a length of 50 mm was collected from the center of the test material (annealed material). The test piece was anodically electrolyzed to dissolve the matrix, precipitates, etc. were extracted, ICP (high frequency inductively coupled plasma) emission analysis was performed using the extracted residue, and the total content of Si and Al in the residue was determined. taking measurement. The anodic electrolysis was performed by constant current electrolysis using an electrolytic solution containing 1% by mass of tartaric acid. Dividing this total content by the mass difference of the test piece before and after dissolution of the matrix by anodic electrolysis (that is, the dissolution amount of the test piece), the total content (mass%) of Si and Al deposited in the matrix is obtained. Calculated. The total content of precipitated Si and Al was subtracted from the total content of Si and Al in the steel material to calculate the total content of dissolved Si and Al. Also, the total amount of residues obtained by dissolving the matrix is divided by the difference in mass of the test piece before and after dissolution of the matrix by anodic electrolysis (dissolution amount of the test piece), and the total content (mass%) of precipitates, etc. )
＜耐水素脆化特性の測定＞
試験材（焼鈍材）および試験材（冷間圧延材）の板厚中心部から平行部の幅２ｍｍ×厚さ２ｍｍ、もしくは幅２ｍｍ×厚さ１ｍｍの板状引張試験片を採取し、水溶液中での陰極チャージ下での低ひずみ速度引張試験により、耐水素脆化特性を評価した。溶液には常温の３％ＮａＣｌ＋３ｇ／Ｌチオシアン酸アンモニウム水溶液を用いて、飽和カロメル電極に対して−１．２（Ｖ）で陰極水素チャージを行いつつ引張試験を行った。ひずみ速度は３×１０−４（ｓ−１）とした。陰極チャージ下の破断伸びを測定し、これを大気中で測定した破断伸びで除して、相対破断伸び（％）を算出した。相対破断伸びが大きい材料ほど、耐水素脆化特性に優れる。本実施形態においては、相対破断伸びが５０％以上の試験材を耐水素脆化特性に優れると判断した。
<Measurement of hydrogen embrittlement resistance>
A plate-shaped tensile test piece having a width of 2 mm × thickness of 2 mm or a width of 2 mm × thickness of 1 mm from the center of the thickness of the test material (annealed material) and the test material (cold rolled material) is collected in an aqueous solution. The hydrogen embrittlement resistance was evaluated by a low strain rate tensile test under cathodic charging. A 3% NaCl + 3 g / L ammonium thiocyanate aqueous solution at room temperature was used as the solution, and a tensile test was performed while performing cathode hydrogen charging at −1.2 (V) against a saturated calomel electrode. The strain rate was 3 × 10 −4 (s −1 ). Relative elongation at break (%) was calculated by measuring the elongation at break under cathodic charge and dividing this by the elongation measured in air. The higher the relative elongation at break, the better the hydrogen embrittlement resistance. In the present embodiment, it was determined that a test material having a relative breaking elongation of 50% or more is excellent in hydrogen embrittlement resistance.
＜機械的特性の測定＞
試験材（焼鈍材）および試験材（冷間圧延材）から試験部の厚さが１〜２ｍｍ、試験部の幅が６ｍｍの板状引張試験片を採取し、JIS Z 2241:2011に従って引張試験を行い、ＴＳ（引張強さ）を求めた。
<Measuring mechanical properties>
From the test material (annealed material) and test material (cold rolled material), a plate-shaped tensile test piece having a thickness of 1 to 2 mm and a width of 6 mm of the test part is collected and subjected to a tensile test according to JIS Z 2241: 2011. And TS (tensile strength) was determined.
表２に、焼鈍条件（冷却条件）と、上記の試験結果を示す。 Table 2 shows the annealing conditions (cooling conditions) and the test results.
表２に示すように、本発明例１〜２７は、焼鈍材および冷間加工材のいずれにおいても、相対破断伸びは５０％以上であり、優れた耐水素脆化特性を有していた。一方、比較例２８および２９は、Ｆｎ１およびＦｎ２の値が低く、耐水素脆化特性に劣っていた。比較例３０および３１は、Ｆｎ１値は本発明で規定される範囲を満たしていたが、炭化物（主としてＭｏ炭化物）が生成したために、Ｆｎ２の値が１．０未満であり、耐水素脆化特性に劣っていた。比較例３２は、Ｃ含有量が０．０１％を超えており、焼鈍時に未固溶の粗大炭化物（主として鉄炭化物）が残存しており、耐水素脆化特性に劣っていた。 As shown in Table 2, Inventive Examples 1 to 27 had an excellent hydrogen embrittlement resistance with a relative breaking elongation of 50% or more in both the annealed material and the cold worked material. On the other hand, Comparative Examples 28 and 29 had low values of Fn1 and Fn2, and were inferior in hydrogen embrittlement resistance. In Comparative Examples 30 and 31, the Fn1 value satisfied the range defined by the present invention, but because carbide (mainly Mo carbide) was generated, the value of Fn2 was less than 1.0, and the hydrogen embrittlement resistance property It was inferior to. In Comparative Example 32, the C content exceeded 0.01%, undissolved coarse carbide (mainly iron carbide) remained during annealing, and the hydrogen embrittlement resistance was inferior.
本発明によれば、耐水素脆化特性に優れた低合金鋼が得られる。 According to the present invention, a low alloy steel excellent in hydrogen embrittlement resistance can be obtained.
Claims (3)
Ｃ：０．０１％以下と、
Ｓｉ：０．０５〜１０．０％およびＡｌ：０．０１〜１０．０％の両方またはいずれか一方と、
Ｐ：０．０２５％以下、
Ｓ：０．０１０％以下、
Ｏ：０．００５％以下、
Ｎ：０．００８％以下、
Ｍｎ：０〜１．０％、
Ｂ：０〜０．００３％、
Ｃｒ：０〜５．０％、
Ｍｏ：０〜５．０％、
Ｖ：０〜５．０％、
Ｗ：０〜５．０％、
Ｎｂ：０〜０．１％、
Ｔｉ：０〜０．１％、
Ｚｒ：０〜０．２％、
Ｈｆ：０〜０．２％、
Ｔａ：０〜０．２％、
Ｃｕ：０〜３．０％、
Ｎｉ：０〜５．０％、
Ｃｏ：０〜３．０％、
Ｃａ：０〜０．０１％、
Ｍｇ：０〜０．０１％、
ＲＥＭ：０〜０．５０％と、
残部：Ｆｅおよび不純物とである化学組成を有し、
下記（１）式から求められるＦｎ１が１．０〜１０．０であり、
下記（２）式から求められるＦｎ２が１．０〜１０．０である、
耐水素脆化特性に優れる低合金鋼。
Ｆｎ１ ＝ Ｓｉ＋Ａｌ （質量％）（１）
Ｆｎ２ ＝ Ｓｉ＋Ａｌ （固溶分の質量％）（２）
ただし、（１）式中の各元素記号は、低合金鋼中に含まれる各元素の含有量（質量％）を意味し、（２）式中の各元素記号は、低合金鋼中に固溶状態で存在する各元素の含有量（質量％）を意味する。 % By mass
C: 0.01% or less,
Si: 0.05 to 10.0% and Al: 0.01 to 10.0% or either one of them,
P: 0.025% or less,
S: 0.010% or less,
O: 0.005% or less,
N: 0.008% or less,
Mn: 0 to 1.0%,
B: 0 to 0.003%,
Cr: 0 to 5.0%,
Mo: 0 to 5.0%,
V: 0 to 5.0%,
W: 0 to 5.0%,
Nb: 0 to 0.1%,
Ti: 0 to 0.1%,
Zr: 0 to 0.2%,
Hf: 0 to 0.2%,
Ta: 0 to 0.2%,
Cu: 0 to 3.0%,
Ni: 0 to 5.0%,
Co: 0 to 3.0%,
Ca: 0 to 0.01%,
Mg: 0 to 0.01%,
REM: 0 to 0.50%,
The balance: having a chemical composition that is Fe and impurities,
Fn1 calculated | required from the following (1) Formula is 1.0-10.0,
Fn2 calculated | required from following (2) Formula is 1.0-10.0,
Low alloy steel with excellent hydrogen embrittlement resistance.
Fn1 = Si + Al (mass%) (1)
Fn2 = Si + Al (mass% of solid solution content) (2)
However, each element symbol in the formula (1) means the content (mass%) of each element contained in the low alloy steel, and each element symbol in the formula (2) is solid in the low alloy steel. It means content (mass%) of each element which exists in a solution state.
Ｍｎ：０．１〜１．０％、
Ｂ：０．０００３〜０．００３％
Ｃｒ：０．０１〜５．０％、
Ｍｏ：０．０１〜５．０％、
Ｖ：０．０１〜５．０％、
Ｗ：０．０１〜５．０％、
Ｎｂ：０．００１〜０．１％、
Ｔｉ：０．００１〜０．１％、
Ｚｒ：０．００１〜０．２％、
Ｈｆ：０．００１〜０．２％、
Ｔａ：０．００１〜０．２％、
Ｃｕ：０．１〜３．０％、
Ｎｉ：０．１〜５．０％、
Ｃｏ：０．１〜３．０％、
Ｃａ：０．０００１〜０．０１％、
Ｍｇ：０．０００１〜０．０１％および
ＲＥＭ：０．０００１〜０．５０％
から選択される一種以上を含有する、
請求項１に記載の低合金鋼。 % By mass
Mn: 0.1 to 1.0%,
B: 0.0003 to 0.003%
Cr: 0.01 to 5.0%,
Mo: 0.01 to 5.0%,
V: 0.01-5.0%,
W: 0.01-5.0%,
Nb: 0.001 to 0.1%,
Ti: 0.001 to 0.1%,
Zr: 0.001 to 0.2%,
Hf: 0.001 to 0.2%,
Ta: 0.001 to 0.2%,
Cu: 0.1 to 3.0%,
Ni: 0.1 to 5.0%,
Co: 0.1-3.0%
Ca: 0.0001 to 0.01%,
Mg: 0.0001 to 0.01% and REM: 0.0001 to 0.50%
Containing one or more selected from
The low alloy steel according to claim 1.
請求項１または２に記載の低合金鋼。 The total amount of precipitates, inclusions and intermetallic compounds is 0.5% by mass or less,
The low alloy steel according to claim 1 or 2.
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Citations (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08134604A (en) * | 1994-11-09 | 1996-05-28 | Nkk Corp | Soft-magnetic material, excellent in magnetic flux density, coercive force, and corrosion resistance and having high electric resistance, and its production |
| JPH09298318A (en) * | 1996-05-02 | 1997-11-18 | Katsutoshi Ono | Thermoelectric conversion element |
| JPH10299803A (en) * | 1997-04-22 | 1998-11-13 | Kobe Steel Ltd | High strength spring favourable in environmental brittleness resistance |
| JP2000045025A (en) * | 1998-05-29 | 2000-02-15 | Sumitomo Special Metals Co Ltd | Production of rolled silicon steel |
| JP2005029889A (en) * | 2003-06-18 | 2005-02-03 | Nippon Steel Corp | High strength low specific gravity steel sheet excellent in ductility, and its production method |
| JP2005068548A (en) * | 2003-02-28 | 2005-03-17 | Nippon Steel Corp | High strength thin steel sheet excellent in hydrogen embitterment resistance and its manufacturing method |
| JP2005273004A (en) * | 2004-02-24 | 2005-10-06 | Nippon Steel Corp | Low-specific-gravity steel sheet excellent in ductility and its production method |
| JP2006176844A (en) * | 2004-12-22 | 2006-07-06 | Nippon Steel Corp | High-strength and low-density steel sheet superior in ductility and fatigue characteristic, and manufacturing method therefor |
| JP2012126943A (en) * | 2010-12-14 | 2012-07-05 | Sumitomo Metal Ind Ltd | Cold-rolled steel sheet for resistance welding, and method for producing the same |
| JP2014080676A (en) * | 2012-09-27 | 2014-05-08 | Hitachi Metals Ltd | PRODUCTION METHOD OF Fe-Al BASED ALLOY BAND-STEEL |
| JP2014198874A (en) * | 2013-03-29 | 2014-10-23 | 株式会社神戸製鋼所 | Steel material excellent in corrosion resistance and magnetic properties and method of producing the same |
| JP2014237879A (en) * | 2013-06-07 | 2014-12-18 | 国立大学法人横浜国立大学 | Method of producing solid-solution alloy, solid-solution alloy, electrical steel sheet and electrical bar steel |
| JP2015045086A (en) * | 2013-07-31 | 2015-03-12 | Ｊｆｅスチール株式会社 | Steel sheet excellent in corrosion resistance of cut end face and manufacturing method therefor |
| CN104805377A (en) * | 2015-05-08 | 2015-07-29 | 南京理工大学 | Low-alloy ultrahigh-strength steel and preparation method thereof |
| JP2016056418A (en) * | 2014-09-10 | 2016-04-21 | 株式会社神戸製鋼所 | Steel material for cold working |
-
2017
- 2017-07-18 JP JP2017139290A patent/JP6972722B2/en active Active
Patent Citations (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08134604A (en) * | 1994-11-09 | 1996-05-28 | Nkk Corp | Soft-magnetic material, excellent in magnetic flux density, coercive force, and corrosion resistance and having high electric resistance, and its production |
| JPH09298318A (en) * | 1996-05-02 | 1997-11-18 | Katsutoshi Ono | Thermoelectric conversion element |
| JPH10299803A (en) * | 1997-04-22 | 1998-11-13 | Kobe Steel Ltd | High strength spring favourable in environmental brittleness resistance |
| JP2000045025A (en) * | 1998-05-29 | 2000-02-15 | Sumitomo Special Metals Co Ltd | Production of rolled silicon steel |
| JP2005068548A (en) * | 2003-02-28 | 2005-03-17 | Nippon Steel Corp | High strength thin steel sheet excellent in hydrogen embitterment resistance and its manufacturing method |
| JP2005029889A (en) * | 2003-06-18 | 2005-02-03 | Nippon Steel Corp | High strength low specific gravity steel sheet excellent in ductility, and its production method |
| JP2005273004A (en) * | 2004-02-24 | 2005-10-06 | Nippon Steel Corp | Low-specific-gravity steel sheet excellent in ductility and its production method |
| JP2006176844A (en) * | 2004-12-22 | 2006-07-06 | Nippon Steel Corp | High-strength and low-density steel sheet superior in ductility and fatigue characteristic, and manufacturing method therefor |
| JP2012126943A (en) * | 2010-12-14 | 2012-07-05 | Sumitomo Metal Ind Ltd | Cold-rolled steel sheet for resistance welding, and method for producing the same |
| JP2014080676A (en) * | 2012-09-27 | 2014-05-08 | Hitachi Metals Ltd | PRODUCTION METHOD OF Fe-Al BASED ALLOY BAND-STEEL |
| JP2014198874A (en) * | 2013-03-29 | 2014-10-23 | 株式会社神戸製鋼所 | Steel material excellent in corrosion resistance and magnetic properties and method of producing the same |
| JP2014237879A (en) * | 2013-06-07 | 2014-12-18 | 国立大学法人横浜国立大学 | Method of producing solid-solution alloy, solid-solution alloy, electrical steel sheet and electrical bar steel |
| JP2015045086A (en) * | 2013-07-31 | 2015-03-12 | Ｊｆｅスチール株式会社 | Steel sheet excellent in corrosion resistance of cut end face and manufacturing method therefor |
| JP2016056418A (en) * | 2014-09-10 | 2016-04-21 | 株式会社神戸製鋼所 | Steel material for cold working |
| CN104805377A (en) * | 2015-05-08 | 2015-07-29 | 南京理工大学 | Low-alloy ultrahigh-strength steel and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| PALM M.: ""Concepts derived from phase diagram studies for the strengthening of Fe-Al-based alloys"", INTERMETALLICS, vol. 13, JPN6021020300, 26 April 2005 (2005-04-26), pages 1286 - 1295, ISSN: 0004516480 * |
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