JP4045977B2 - H-shaped steel with projections excellent in hot workability and toughness and method for producing the same - Google Patents
H-shaped steel with projections excellent in hot workability and toughness and method for producing the same Download PDFInfo
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Description
【０００１】
【発明の属する技術分野】
本発明は、フランジ外面に突起を有する突起付Ｈ形鋼およびその製造方法に関し、特にその熱間加工性と靱性の有利な向上を図ろうとするものである。
【０００２】
【従来の技術】
路面覆工板として用いられるＨ形鋼は、路上を通行する自動車や歩行者のスリップや転倒を防止するために、フランジ表面に突起が設けられている。
また、鉄筋コンクリート構造物において、強度的に鉄筋の過密配筋が必要となる場合、この過密配筋によって施工性が悪化し、工期が長期化するだけでなく、コスト高となるため、鉄筋の代わりに突起を設けたＨ形鋼をフランジ外面に用いる場合がある。
【０００３】
このようなフランジ外面に突起を有するＨ形鋼は、ロール表面に溝を有するロールを用いて、熱間圧延を施すことにより製造される。しかしながら、熱間圧延によってＨ形鋼に突起を安定して形成するのは容易ではない。
例えば、特許文献１では、覆工板に用いられる突起付Ｈ形鋼を製造する場合、突起を形成するための溝付ロールの溝の配置や圧下量の配分などを適正化することによって、その安定製造を図っている。
【０００４】
ところで、従来の突起付Ｈ形鋼において、覆工板として用いられる場合の必要性能は、JIS G 3101「一般構造用圧延鋼材」に規定されている SS400の性能で満足されていた。
また、鉄筋の代替として用いられる場合には、JIS G 3106「溶接構造用圧延鋼材」に規定されている SM490YAの性能で満足されていた。
【０００５】
しかしながら、上記した SS400およびSM490YA では、その性能に関し、引張強度、耐力、延びといった機械的性質については保証すべき基準値が設けられているものの、鋼材の靱性を表わす衝撃吸収エネルギー値については特に要求されていない。
そのため、従来の突起付Ｈ形鋼は、靱性に関しては必ずしも優れた性能を有しているわけではなかった。
【０００６】
【特許文献１】
特開昭50−124861号公報（特許請求の範囲）
【０００７】
【発明が解決しようとする課題】
ところで、近年、鉄筋の代替材として使用される突起付Ｈ形鋼に関しては、寒冷地で使用されたり、また従来よりも厚肉のＨ形鋼の適用が求められるようになってきた。
これらの用途に適用する場合には、構造体の性能を保証するために、構造体の主要部材である突起付Ｈ形鋼に対して、靱性の保証が要求されるようになってきた。
【０００８】
従来の突起付Ｈ形鋼は、 SS400やSM490YA などの機械的性能を有する範囲で、できるだけ低コストで突起を安定して形成できるような成分と製造方法が採用されてきた。
SS400 やSM490YA の機械的性能を保証するには、特別な合金を多く含まない一般的な炭素鋼で十分であるが、突起を安定して形成するには、突起を有しないＨ形鋼に比べて高温での圧延が必要となるため、一般的な炭素鋼では十分な靱性が得られないという問題があった。
すなわち、一般的な炭素鋼を高温で圧延すると、オーステナイトの粗粒再結晶域で圧延が終了するため、変態完了後のフェライト・パーライト組織が粗粒組織となり、その結果、十分な靱性が得られなかったのである。
【０００９】
本発明は、上記の問題を有利に解決するもので、高温での圧延など熱間加工性を阻害することなしに、靱性を効果的に向上させた突起付Ｈ形鋼を、その有利な製造方法と共に提案することを目的とする。
【００１０】
【課題を解決するための手段】
本発明は、上記の課題を解決するために、突起を形成するのに必要かつ十分な圧延温度を定め、この圧延温度の下でも十分な靱性値が得られるように、鋼材の成分組成を調整すると共に、圧延後の冷却条件を規定したもので、必要最小限のコストアップで、安定した突起の形成と、引張り強さ、 0.2％耐力および延びの確保、さらには靱性（衝撃吸収エネルギー値で評価）の改善を達成したものである。
【００１１】
すなわち、本発明は、
Ｃ：0.12〜0.15mass％、
Si：0.25〜0.40mass％、
Mn：1.40〜1.60mass％、
Nb：0.020 〜0.040 mass％、
Ｖ：0.015 〜0.040 mass％および
Ni：0.10〜0.30mass％
を含有し、残部はFeおよび不可避的不純物の組成になり、かつ０℃における衝撃吸収エネルギー VＥ0 が27Ｊ以上であることを特徴とする熱間加工性および靱性に優れた突起付Ｈ形鋼である。
【００１２】
また、本発明は、
Ｃ：0.12〜0.15mass％、
Si：0.25〜0.40mass％、
Mn：1.40〜1.60mass％、
Nb：0.020 〜0.040 mass％、
Ｖ：0.015 〜0.040 mass％および
Ni：0.10〜0.30mass％
を含有し、残部はFeおよび不可避的不純物の組成になる鋼材を、熱間圧延によりＨ型鋼に成形するに際し、フランジ外面に突起を付与する仕上げ圧延温度を 800℃以上にすると共に、その後の冷却を、冷却開始時のフランジ温度：800 ℃以上、冷却速度：６〜40℃/s、冷却停止温度：500 〜750 ℃の条件下で行うことを特徴とする熱間加工性および靱性に優れた突起付Ｈ形鋼の製造方法である。
【００１３】
【発明の実施の形態】
以下、本発明を具体的に説明する。
本発明によれば、フランジ厚が16mm以上の突起付Ｈ形鋼において、突起を形成する際の仕上げ圧延温度を 800℃以上とし、この条件下でも０℃における衝撃吸収エネルギー VＥ0 ：27Ｊ以上を保証するために、以下のように成分組成を調整すると共に、製造条件を規定する。
Ｃ：0.12〜0.15mass％
Ｃは、低コストで強度を得るのに有利な元素であるので、0.12mass％以上含有させるものとした。しかしながら、含有量が0.15mass％を超えると靱性の低下を招くので、Ｃは0.12〜0.15mass％の範囲に限定した。
なお、Ｃ量を低く抑えたことによる機械的強度の低下については、後述するNbおよびＶで補償するものとした。
【００１４】
Si：0.25〜0.40mass％
Siは、脱酸剤として0.25mass％以上含有させる。しかしながら、含有量が0.40mass％を超えると靱性の低下を招くので、Siは0.25〜0.40mass％の範囲に限定した。
【００１５】
Mn：1.40〜1.60mass％
Mnは、強度と靱性を向上させるために1.40mass％以上含有させる。しかしながら、含有量が1.60mass％を超えるとJIS 規格値外れとなるので、Mnは1.40〜1.60mass％の範囲に限定した。
【００１６】
Nb：0.020 〜0.040 mass％
Nbは、炭窒化物を形成することによって、引張り強さや降伏点の向上に有効に寄与するが、含有量が 0.020mass％に満たないとその添加効果に乏しく、一方 0.040mass％を超えると靱性が劣化するので、Nbは 0.020〜0.040 mass％の範囲で含有させるものとした。
【００１７】
Ｖ：0.015 〜0.040 mass％
Ｖも、Nbと同様、炭窒化物の形成によって、引張り強さや降伏点を向上させる有用元素であるが、含有量が 0.015mass％に満たないとその添加効果に乏しく、一方 0.040mass％を超えると延びが低下するので、Ｖは 0.015〜0.040 mass％の範囲で含有させるものとした。
【００１８】
Ni：0.10〜0.30mass％
Niは、靱性の向上のために0.10mass％以上含有させる。しかしながら、含有量の増加と共にコストアップの弊害が生じるので、Niは0.10〜0.30mass％の範囲で含有させるものとした。
【００１９】
次に、本発明の製造条件について説明する。
鋼の溶製法および鋳造法については特に制限はなく、従来公知の方法いずれもが適合する。また、Ｈ型鋼に成形するための熱間圧延条件も特に制限されることはなく、常法に従って行えば良い。
但し、フランジ外面に突起を付与するための仕上げ圧延温度およびその後の冷却（加速冷却）については、以下の条件を満足させる必要がある。
【００２０】
仕上げ圧延温度：800 ℃以上
この仕上げ温度が 800℃に満たないと、安定して突起を形成することが難しいので、 800℃以上に限定した。
【００２１】
冷却開始時のフランジ温度：800 ℃以上
仕上げ圧延時の鋼材の温度は、突起を安定して形成する目的から、上述したとおり 800℃以上としているため、圧延直後の鋼材のフランジ温度も 800℃以上となる。本発明では、圧延直後に鋼材の冷却を開始することによって生産能率の低下を防止することを目的としているので、冷却開始時のフランジ温度も 800℃以上となる。
【００２２】
冷却速度：６〜40℃/s
冷却速度は、これを制御することによって変態挙動を制御し、所望の組織形態とすることができる。フェライト変態によるフェライト・パーライト組織を得て、フェライト分率の向上により引張り強さや降伏点を向上させるためには、６℃/s以上の冷却速度が必要である。しかしながら、冷却速度が40℃/sを超えて大きくなると変態挙動が変化し、ベイナイト変態あるいはマルテンサイト変態が生じて引張り強さが上昇し過ぎる弊害が生じるので、冷却速度は６〜40℃/sの範囲に制限した。
【００２３】
冷却停止温度：500 〜750 ℃
加速冷却における冷却停止温度を低下させることは、フェライト・パーライト変態において組織を微細化する効果があり、靱性の向上と共に引張り強さや降伏点の向上を図るためには、冷却停止温度は 750℃以下とする必要がある。しかしながら、冷却停止温度が 500℃未満になるとフランジの傘折れ形状が大きくなるだけでなく、引張り強さが上昇し過ぎる弊害が生じるので、冷却停止温度は 500〜750 ℃の範囲に制御するものとした。
【００２４】
上記したような成分調整および加速冷却を行うことにより、フランジ厚が16mm以上の突起付Ｈ形鋼において、仕上げ圧延温度：800 ℃以上の条件下で安定して突起が形成できるだけでなく、引張り強さが 490 MPa以上、610 MPa 以下、降伏点が 355 MPa以上、延びが19％以上、そして０℃における衝撃吸収エネルギー VＥ0 が27Ｊ以上という優れた機械的性能を得ることができる。
【００２５】
なお、本発明で対象とする突起付Ｈ形鋼は、そのフランジ厚が特に限定されることはなく、本発明は、突起高さの形成効率が低下するとされる、フランジ厚が16mm以上（好ましくは42mm以下）の厚肉のＨ形鋼にも好適に適用することができる。
【００２６】
【実施例】
表１に示す成分組成になる鋼材を、同じく表１に示す種々の仕上げ温度、冷却開始温度、冷却速度および冷却停止温度条件下で熱間圧延することにより、断面寸法が 340×328 ×30×35（mm）の突起付Ｈ形鋼を製造した。
かくして得られた突起付Ｈ形鋼の突起高さ、引張り強さ、降伏点、延びおよび０℃における衝撃吸収エネルギー VＥ0 について調べた結果を、表１に併記する。
なお、突起高さの要求性能下限値は 2.1mmである。
【００２７】
【表１】
同表から明かなように、発明例はいずれも、突起高さが2.1 mm以上を満足するだけでなく、引張り強さ≧490 MPa 、降伏点≧355 MPa 、延び≧19％および０℃における衝撃吸収エネルギー VＥ0 ≧27Ｊを満足しており、衝撃靱性値を保証した突起付Ｈ形鋼として十分使用に耐え得る。
【００２９】
【発明の効果】
かくして、本発明によれば、熱間加工性を阻害することなしに、靱性を効果的に向上させた突起付Ｈ形鋼を得ることができる。
従って、本発明によれば、衝撃靱性値が必要とされる寒冷地での突起付Ｈ形鋼の使用が可能になる。また、フランジ厚16mm以上の突起付Ｈ形鋼を鉄筋の代替としてコンクリート構造体の鉄骨に使用できる。これらにより、従来は鉄筋の過密配筋により、高コスト、長工期で施工きれていたコンクリート構造体が、低コスト、短工期で施工可能になり、大きな経済効果が得られる。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a H-shaped steel with protrusions having protrusions on the outer surface of a flange and a method for manufacturing the same, and particularly aims to advantageously improve hot workability and toughness.
[0002]
[Prior art]
The H-section steel used as a road surface covering plate is provided with protrusions on the flange surface in order to prevent slipping and falling of automobiles and pedestrians passing on the road.
In addition, in a reinforced concrete structure, if reinforcing bar reinforcement is required due to strength, the overwork arrangement deteriorates workability and not only lengthens the construction period but also increases the cost. In some cases, H-shaped steel provided with protrusions on the flange outer surface is used.
[0003]
Such H-shaped steel having protrusions on the outer surface of the flange is manufactured by hot rolling using a roll having grooves on the roll surface. However, it is not easy to stably form protrusions on the H-shaped steel by hot rolling.
For example, in Patent Document 1, when manufacturing a H-shaped steel with a projection used for a lining plate, by optimizing the arrangement of the groove of the grooved roll for forming the projection and the distribution of the reduction amount, We are aiming for stable production.
[0004]
By the way, in the conventional H-shaped steel with protrusions, the required performance when used as a lining plate was satisfied by the performance of SS400 defined in JIS G 3101 “General structural rolled steel”.
In addition, when used as a substitute for reinforcing bars, the performance of SM490YA specified in JIS G 3106 “Rolled steel for welded structures” was satisfied.
[0005]
However, the above-mentioned SS400 and SM490YA have standard values that should be guaranteed for their mechanical properties such as tensile strength, proof stress, and elongation, but are particularly required for the impact absorption energy value that represents the toughness of steel. It has not been.
Therefore, the conventional H-shaped steel with protrusions does not necessarily have excellent performance with respect to toughness.
[0006]
[Patent Document 1]
Japanese Patent Application Laid-Open No. 50-124861 (Claims)
[0007]
[Problems to be solved by the invention]
By the way, in recent years, with respect to the H-shaped steel with projections used as an alternative material for reinforcing bars, it has been demanded to use H-shaped steel that is used in cold districts or that is thicker than before.
When applied to these applications, in order to guarantee the performance of the structure, it has been required to guarantee toughness for the H-shaped steel with protrusions, which is the main member of the structure.
[0008]
In conventional H-shaped steel with protrusions, components and manufacturing methods have been adopted so that protrusions can be stably formed at as low a cost as possible within the range of mechanical performance such as SS400 and SM490YA.
In order to guarantee the mechanical performance of SS400 and SM490YA, general carbon steel that does not contain many special alloys is sufficient, but in order to form protrusions stably, compared to H-section steel without protrusions. Since rolling at a high temperature is necessary, there is a problem that sufficient toughness cannot be obtained with general carbon steel.
In other words, when a general carbon steel is rolled at a high temperature, the rolling finishes in the austenite coarse grain recrystallization region, so the ferrite pearlite structure after the transformation is completed becomes a coarse grain structure, and as a result, sufficient toughness is obtained. There was no.
[0009]
The present invention advantageously solves the above-mentioned problems, and advantageously provides a protuberance-shaped H-section steel having effectively improved toughness without impairing hot workability such as rolling at high temperatures. It is intended to be proposed along with the method.
[0010]
[Means for Solving the Problems]
In order to solve the above-mentioned problems, the present invention determines the rolling temperature necessary and sufficient for forming the protrusions, and adjusts the composition of the steel material so that a sufficient toughness value can be obtained even under this rolling temperature. In addition, the cooling conditions after rolling are specified, and the formation of stable protrusions, the securing of tensile strength, 0.2% proof stress and elongation, and toughness (impact absorption energy value) at the minimum necessary cost increase. Evaluation) has been achieved.
[0011]
That is, the present invention
C: 0.12-0.15 mass%
Si: 0.25 ~ 0.40mass%,
Mn: 1.40-1.60 mass%
Nb: 0.020 to 0.040 mass%,
V: 0.015-0.040 mass% and
Ni: 0.10 ~ 0.30mass%
With a balance of Fe and inevitable impurities, and a shock-absorbing energy V E 0 at 0 ° C. of 27 J or more, and a H-shaped steel with a protrusion excellent in hot workability and toughness It is.
[0012]
The present invention also provides:
C: 0.12-0.15 mass%
Si: 0.25 ~ 0.40mass%,
Mn: 1.40-1.60 mass%
Nb: 0.020 to 0.040 mass%,
V: 0.015-0.040 mass% and
Ni: 0.10 ~ 0.30mass%
When the steel material containing Fe and the inevitable impurities is formed into H-shaped steel by hot rolling, the finish rolling temperature for imparting protrusions to the flange outer surface is set to 800 ° C or higher and the subsequent cooling is performed. Is excellent in hot workability and toughness characterized by being performed under the conditions of a flange temperature at the start of cooling: 800 ° C. or higher, a cooling rate: 6-40 ° C./s, and a cooling stop temperature: 500-750 ° C. It is a manufacturing method of H shape steel with a projection.
[0013]
DETAILED DESCRIPTION OF THE INVENTION
The present invention will be specifically described below.
According to the present invention, in the H-shaped steel with protrusions having a flange thickness of 16 mm or more, the finish rolling temperature when forming the protrusions is set to 800 ° C. or higher, and even under this condition, the impact absorption energy V E 0 at 27 ° C. is 27 J or higher. In order to ensure the above, the component composition is adjusted as follows, and the production conditions are specified.
C: 0.12-0.15 mass%
C is an element advantageous for obtaining strength at a low cost, so it was contained in an amount of 0.12 mass% or more. However, if the content exceeds 0.15 mass%, the toughness is reduced, so C is limited to the range of 0.12 to 0.15 mass%.
In addition, about the fall of the mechanical strength by suppressing C amount low, it shall compensate with Nb and V mentioned later.
[0014]
Si: 0.25 ～ 0.40mass%
Si is contained as a deoxidizer in an amount of 0.25 mass% or more. However, if the content exceeds 0.40 mass%, the toughness is reduced, so Si is limited to the range of 0.25 to 0.40 mass%.
[0015]
Mn: 1.40 to 1.60 mass%
Mn is contained in an amount of 1.40 mass% or more in order to improve strength and toughness. However, when the content exceeds 1.60 mass%, the JIS standard value is lost, so Mn is limited to the range of 1.40 to 1.60 mass%.
[0016]
Nb: 0.020 to 0.040 mass%
Nb contributes effectively to the improvement of tensile strength and yield point by forming carbonitride, but if the content is not less than 0.020 mass%, its additive effect is poor, while if it exceeds 0.040 mass%, toughness Therefore, Nb was included in the range of 0.020 to 0.040 mass%.
[0017]
V: 0.015-0.040 mass%
V, like Nb, is a useful element that improves the tensile strength and yield point by the formation of carbonitrides. However, if the content is less than 0.015 mass%, the effect of addition is poor, while it exceeds 0.040 mass%. Therefore, V is contained in the range of 0.015 to 0.040 mass%.
[0018]
Ni: 0.10 ~ 0.30mass%
Ni is contained in an amount of 0.10 mass% or more for improving toughness. However, since the adverse effect of increasing the cost occurs as the content increases, Ni is included in the range of 0.10 to 0.30 mass%.
[0019]
Next, the manufacturing conditions of the present invention will be described.
There is no restriction | limiting in particular about the melting method and casting method of steel, All the conventionally well-known methods are suitable. Further, the hot rolling conditions for forming the H-shaped steel are not particularly limited, and may be performed according to a conventional method.
However, it is necessary to satisfy the following conditions for the finish rolling temperature and subsequent cooling (accelerated cooling) for providing protrusions on the flange outer surface.
[0020]
Finishing rolling temperature: 800 ° C or higher If this finishing temperature is less than 800 ° C, it is difficult to stably form protrusions.
[0021]
Flange temperature at the start of cooling: 800 ° C or higher Since the temperature of steel during finish rolling is 800 ° C or higher as described above for the purpose of stably forming protrusions, the flange temperature of steel immediately after rolling is also 800 ° C or higher. It becomes. In the present invention, since the purpose is to prevent the reduction of the production efficiency by starting the cooling of the steel material immediately after rolling, the flange temperature at the start of the cooling becomes 800 ° C. or more.
[0022]
Cooling rate: 6 ~ 40 ℃ / s
By controlling the cooling rate, the transformation behavior can be controlled by controlling this, and the desired tissue morphology can be obtained. In order to obtain a ferrite / pearlite structure by ferrite transformation and improve the tensile strength and yield point by improving the ferrite fraction, a cooling rate of 6 ° C./s or more is required. However, when the cooling rate increases beyond 40 ° C./s, the transformation behavior changes, and the bainite transformation or martensite transformation occurs, resulting in an adverse effect of excessive increase in tensile strength. Therefore, the cooling rate is 6-40 ° C./s. Limited to the range.
[0023]
Cooling stop temperature: 500-750 ° C
Decreasing the cooling stop temperature in accelerated cooling has the effect of refining the structure in the ferrite-pearlite transformation, and the cooling stop temperature is 750 ° C or lower in order to improve the toughness and the tensile strength and yield point. It is necessary to. However, if the cooling stop temperature is less than 500 ° C, not only will the flange bend shape increase, but the tensile strength will increase too much, so the cooling stop temperature should be controlled in the range of 500-750 ° C. did.
[0024]
By adjusting the components as described above and accelerating cooling, in the H-shaped steel with protrusions with a flange thickness of 16 mm or more, not only can the protrusions be stably formed at the finish rolling temperature of 800 ° C or more, but also the tensile strength It is possible to obtain excellent mechanical performance with a thickness of 490 MPa or more and 610 MPa or less, a yield point of 355 MPa or more, an elongation of 19% or more, and an impact absorption energy V E 0 at 0 ° C. of 27 J or more.
[0025]
In addition, the flange thickness of the H-shaped steel with protrusions targeted in the present invention is not particularly limited, and the present invention has a flange thickness of 16 mm or more (preferably, the formation efficiency of the protrusion height is reduced) Can be suitably applied to a thick H-shaped steel having a thickness of 42 mm or less.
[0026]
【Example】
A steel material having the composition shown in Table 1 is hot-rolled under various finishing temperatures, cooling start temperatures, cooling rates, and cooling stop temperature conditions shown in Table 1 to obtain a cross-sectional dimension of 340 × 328 × 30 ×. A 35 mm-shaped H-shaped steel with a protrusion was manufactured.
Table 1 shows the results of examining the protrusion height, tensile strength, yield point, elongation and impact absorption energy V E 0 at 0 ° C. of the H-shaped steel with protrusions thus obtained.
The lower limit of the required performance of the protrusion height is 2.1 mm.
[0027]
[Table 1]
As is clear from the table, all of the inventive examples not only satisfy the projection height of 2.1 mm or more, but also have a tensile strength ≧ 490 MPa, a yield point ≧ 355 MPa, an elongation ≧ 19%, and an impact at 0 ° C. The absorbed energy V E 0 ≧ 27J is satisfied, and it can be sufficiently used as a H-shaped steel with protrusions that guarantees an impact toughness value.
[0029]
【The invention's effect】
Thus, according to the present invention, it is possible to obtain a H-shaped steel with projections with effectively improved toughness without impairing hot workability.
Therefore, according to the present invention, it becomes possible to use the H-shaped steel with projections in a cold district where an impact toughness value is required. In addition, H-shaped steel with protrusions with a flange thickness of 16 mm or more can be used for steel frames in concrete structures as an alternative to reinforcing bars. As a result, a concrete structure that has conventionally been constructed with high cost and a long construction period can be constructed with a low cost and a short construction period due to overcrowding of the reinforcing bars, and a great economic effect can be obtained.
Claims (2)
Si：0.25〜0.40mass％、
Mn：1.40〜1.60mass％、
Nb：0.020 〜0.040 mass％、
Ｖ：0.015 〜0.040 mass％および
Ni：0.10〜0.30mass％
を含有し、残部はFeおよび不可避的不純物の組成になり、かつ０℃における衝撃吸収エネルギー VＥ0 が27Ｊ以上であることを特徴とする熱間加工性および靱性に優れた突起付Ｈ形鋼。C: 0.12-0.15 mass%
Si: 0.25 ~ 0.40mass%,
Mn: 1.40-1.60 mass%
Nb: 0.020 to 0.040 mass%,
V: 0.015-0.040 mass% and
Ni: 0.10 ~ 0.30mass%
With a balance of Fe and inevitable impurities, and a shock-absorbing energy V E 0 at 0 ° C. of 27 J or more. .
Si：0.25〜0.40mass％、
Mn：1.40〜1.60mass％、
Nb：0.020 〜0.040 mass％、
Ｖ：0.015 〜0.040 mass％および
Ni：0.10〜0.30mass％
を含有し、残部はFeおよび不可避的不純物の組成になる鋼材を、熱間圧延によりＨ型鋼に成形するに際し、フランジ外面に突起を付与する仕上げ圧延温度を 800℃以上にすると共に、その後の冷却を、冷却開始時のフランジ温度：800 ℃以上、冷却速度：６〜40℃/s、冷却停止温度：500 〜750 ℃の条件下で行うことを特徴とする熱間加工性および靱性に優れた突起付Ｈ形鋼の製造方法。C: 0.12-0.15 mass%
Si: 0.25 ~ 0.40mass%,
Mn: 1.40-1.60 mass%
Nb: 0.020 to 0.040 mass%,
V: 0.015-0.040 mass% and
Ni: 0.10 ~ 0.30mass%
When the steel material containing Fe and the inevitable impurities is formed into H-shaped steel by hot rolling, the finish rolling temperature for imparting protrusions to the flange outer surface is set to 800 ° C or higher and the subsequent cooling is performed. Is excellent in hot workability and toughness characterized by being performed under the conditions of a flange temperature at the start of cooling: 800 ° C. or higher, a cooling rate: 6-40 ° C./s, and a cooling stop temperature: 500-750 ° C. Manufacturing method of H-shaped steel with protrusion.
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| KR20210118925A (en) | 2019-01-31 | 2021-10-01 | 제이에프이 스틸 가부시키가이샤 | H-beam with projections and manufacturing method thereof |
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|---|---|---|---|---|
| KR101167389B1 (en) | 2010-02-26 | 2012-07-19 | 현대제철 주식회사 | Steel for structure, and method for producing the same |
| CN105018839B (en) * | 2015-08-14 | 2017-05-03 | 武钢集团昆明钢铁股份有限公司 | 420 MPa grade high-performance anti-shock H-type steel and preparation method thereof |
| WO2020158822A1 (en) * | 2019-01-31 | 2020-08-06 | Ｊｆｅスチール株式会社 | H-shaped steel having protrusions, and manufacturing method for same |
| JP7184062B2 (en) * | 2020-03-12 | 2022-12-06 | Ｊｆｅスチール株式会社 | H-section steel with ridges and method for manufacturing the same |
| JP7347361B2 (en) * | 2020-07-31 | 2023-09-20 | Ｊｆｅスチール株式会社 | H-shaped steel with protrusions and its manufacturing method |
| CN114959458A (en) * | 2022-05-05 | 2022-08-30 | 包头钢铁（集团）有限责任公司 | Manufacturing method of hot-rolled H-shaped steel for DH36 ocean engineering structure |
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| KR20210118925A (en) | 2019-01-31 | 2021-10-01 | 제이에프이 스틸 가부시키가이샤 | H-beam with projections and manufacturing method thereof |
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