JPH06340951A - High strength rail excellent in toughness and its production - Google Patents
High strength rail excellent in toughness and its productionInfo
- Publication number
- JPH06340951A JPH06340951A JP5261193A JP5261193A JPH06340951A JP H06340951 A JPH06340951 A JP H06340951A JP 5261193 A JP5261193 A JP 5261193A JP 5261193 A JP5261193 A JP 5261193A JP H06340951 A JPH06340951 A JP H06340951A
- Authority
- JP
- Japan
- Prior art keywords
- rail
- toughness
- pearlite
- temp
- heat treatment
- 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.)
- Pending
Links
Landscapes
- Heat Treatment Of Articles (AREA)
Abstract
Description
【0001】[0001]
【産業上の利用分野】本発明は、レール鋼のパーライト
組織を微細化して靭性の向上を図った高強度レールおよ
びその製造法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength rail in which the pearlite structure of rail steel is refined to improve toughness and a method for producing the same.
【0002】[0002]
【従来の技術】近年、鉄道輸送は高荷重化、高速化が指
向され、レールに要求される特性がますます厳しくなっ
ている。高荷重鉄道では急曲線区間の摩耗対策、レール
頭部内部疲労損傷対策が要求され、高速鉄道では主とし
て直線区間の表面損傷が課題として挙げられている。こ
れらに加えて、寒冷地においては、冬季にレール破断が
集中的に発生する傾向が認められており、寒冷地鉄道で
のレール材の靭性改善は、安全な鉄道輸送に欠かせない
特性になっている。高強度レールの靭性改善の方策とし
ては以下の方法が考えられる。 (1)普通圧延後一旦室温まで冷却したレール頭部を低
温度で再加熱した後加速冷却する方法。 (2)制御圧延によりオーステナイト粒を微細化した後
レール頭部を加速冷却する方法。 (3)制御圧延した後、パーライト変態前で低温度に再
加熱し、その後加速冷却する方法。2. Description of the Related Art In recent years, railway transportation has been aimed at higher loads and higher speeds, and the characteristics required for rails have become increasingly severe. For heavy-duty railways, measures against wear on sharp curves and internal fatigue damage to rail heads are required. On high-speed railways, surface damage mainly on straight sections is cited as an issue. In addition to these, it is recognized that rail rupture tends to occur intensively in winter in cold regions, and improving the toughness of rail materials in cold region railways is a characteristic that is essential for safe rail transportation. ing. The following methods can be considered as measures to improve the toughness of high strength rails. (1) A method in which a rail head that has been once cooled to room temperature after normal rolling is reheated at a low temperature and then accelerated cooling is performed. (2) A method of accelerating and cooling the rail head after refining austenite grains by controlled rolling. (3) A method in which after controlled rolling, it is reheated to a low temperature before pearlite transformation and then accelerated cooling is performed.
【0003】[0003]
【発明が解決しようとする課題】上記方法の(1)で
は、大幅な靭性改善のためには特開昭55−12523
1号公報に記載されているような通常の加熱温度よりも
低い850℃以下の温度に再加熱し、オーステナイト粒
度を微細にすることによって靭性を改善しようとするも
ので、低温度で加熱してかつレール頭部内部まで加熱を
深めようとすると、投入熱量を下げて長時間加熱する必
要がある。このため熱処理生産性を著しく阻害し製造コ
ストを高める難点がある。また、(2)の方法は特開昭
52−138427号公報および特開昭52−1384
28号公報に記載されているように、圧延時のオーステ
ナイト粒の細粒化によって靭性の向上を図ろうとする
と、高温での大圧下が要求され、レール圧延機の能力あ
るいはレールの形状制御の観点からも問題を含んでい
る。さらに(3)の方法は、特公平4−4371号公報
に記載されているように、800℃以下で5%以上の圧
延を実施した後、再度750〜900℃に加熱すること
によりオーステナイト粒を微細にしようとする方法であ
り、圧延後に低温再加熱のための加熱炉を必要とするた
め作業性、生産性、製造コストの観点から問題が多い。In the above method (1), in order to significantly improve the toughness, JP-A-55-12523 is used.
It is intended to improve the toughness by reheating to a temperature of 850 ° C. or lower, which is lower than the normal heating temperature as described in JP-A No. 1, to improve the toughness, and heating at a low temperature. Moreover, if it is attempted to deepen the heating to the inside of the rail head, it is necessary to lower the amount of heat input and heat for a long time. Therefore, there is a problem that heat treatment productivity is significantly impaired and manufacturing cost is increased. The method (2) is disclosed in JP-A-52-138427 and JP-A-52-1384.
As described in Japanese Patent Publication No. 28, in order to improve the toughness by refining the austenite grains during rolling, large reduction at high temperature is required, and the ability of the rail rolling mill or the shape control of the rail is controlled. It also contains problems. Furthermore, the method of (3), as described in Japanese Patent Publication No. 4-4371, carries out rolling of 5% or more at 800 ° C. or less and then heats it again to 750 to 900 ° C. to form austenite grains. This is a method for making it fine, and since it requires a heating furnace for low-temperature reheating after rolling, there are many problems from the viewpoint of workability, productivity, and manufacturing cost.
【0004】[0004]
【課題を解決するための手段】本発明は上記の発明とは
根本的に異なり、重量%で C :0.55〜0.85%、 Si:0.20〜1.
20%、Mn:0.50〜1.50%、 S :0.0
06〜0.035%、Cr:0.1〜1.0%、
V :0.01〜1.0% を含有し、残部が鉄および不可避的不純物からなるレー
ル鋼でかつオーステナイト粒内のMnSを核としたパー
ライトが存在することを特徴とする靭性に優れた高強度
レールに関するものである。本発明では、従来オーステ
ナイト粒界のみからしか生成しないといわれていたパー
ライト変態を、オーステナイト粒内のMnSにパーライ
ト変態の核となるV炭化物を配して、オーステナイト粒
内からもパーライト変態を生成させることを特徴として
おり、粒界から変態するパーライトに加えて、粒内から
生成したパーライトによって著しくパーライト組織が微
細化し、これにともなって、大幅な靭性の改善を図るこ
とができる。The present invention is fundamentally different from the above-mentioned invention, in which C: 0.55 to 0.85% by weight, Si: 0.20 to 1.
20%, Mn: 0.50 to 1.50%, S: 0.0
06-0.035%, Cr: 0.1-1.0%,
V: 0.01-1.0%, the balance being a rail steel consisting of iron and unavoidable impurities, and the presence of pearlite having MnS in the austenite grains as the core, excellent in toughness and high. It concerns strength rails. In the present invention, the pearlite transformation, which has been conventionally said to be generated only from the austenite grain boundaries, is arranged with MnS in the austenite grains with V carbide serving as the nucleus of the pearlite transformation to generate the pearlite transformation from the austenite grains. In addition to the pearlite transformed from the grain boundary, the pearlite structure is remarkably refined by the pearlite generated from within the grain, and accordingly, the toughness can be significantly improved.
【0005】これに加えて前記組成からなるレール鋼に
対して通常圧延後あるいはレール頭部もしくは底部も含
めて通常温度に再加熱した後、冷却過程でオーステナイ
ト域温度から冷却する際に700〜500℃の間を1〜
5℃/secで加速冷却する方法を付与することによって、
オーステナイト粒内のMnSを核とするパーライトの変
態温度を低下せしめ、MnSを核とするパーライトによ
る組織微細化を通じての靭性改善をより顕著にすること
が可能である。すなわち、図1に示すように、V添加な
しの場合の加速冷却による靭性改善の程度に比べ、Vを
添加し粒内パーライトを生成させた場合の加速冷却によ
る靭性改善の程度の方が大幅に大きい。また、加速冷却
による高強度化によって耐摩耗性にも優れた高強度レー
ルを製造することができる。In addition to this, the rail steel having the above composition is usually rolled or reheated to a normal temperature including the rail head or bottom, and then 700 to 500 is used for cooling from the austenite region temperature in the cooling process. 1 to between ℃
By adding a method of accelerated cooling at 5 ° C / sec,
It is possible to lower the transformation temperature of pearlite having MnS as a nucleus in the austenite grains, and to further improve the toughness through the refinement of the structure by pearlite having MnS as a nucleus. That is, as shown in FIG. 1, the degree of improvement in toughness by accelerated cooling when V is added and intragranular pearlite is significantly greater than the degree of improvement in toughness by accelerated cooling when V is not added. large. In addition, high strength rails having excellent wear resistance can be manufactured by increasing the strength by accelerated cooling.
【0006】[0006]
【作用】以下に本発明について詳細に説明する。先ず、
レールの化学成分を前述のように定めた理由について説
明する。Cは高強度化およびパーライト組織生成のため
の必須元素であり、また耐摩耗性に対しても一義的に効
果を示す元素であるが0.55%未満ではオーステナイ
ト粒界に耐摩耗性および耐損傷性に好ましくない初析フ
ェライトが多量に生成し、また0.85%を超えるとオ
ーステナイト粒界を脆化させる有害な初析セメンタイト
を生成させるばかりか、レール頭部熱処理層や溶接部の
微小偏析部にマルテンサイトが生成し、靭性を著しく損
なうため0.55〜0.85%に限定した。The present invention will be described in detail below. First,
The reason for setting the chemical composition of the rail as described above will be explained. C is an essential element for strengthening and forming a pearlite structure, and is an element that also has a unique effect on wear resistance, but if it is less than 0.55%, wear resistance and resistance to austenite grain boundaries are obtained. A large amount of proeutectoid ferrite, which is unfavorable to damage, is generated, and when it exceeds 0.85%, not only harmful proeutectoid cementite that embrittles the austenite grain boundaries is generated, but also minute amounts of rail head heat treatment layers and welds Martensite is generated in the segregated portion and the toughness is significantly impaired, so the content is limited to 0.55 to 0.85%.
【0007】Siはパーライト組織中のフェライト相へ
の固溶体硬化による高強度化に寄与するばかりか、わず
かながらレール鋼の靭性改善にも貢献する。またSiは
MnとともにMnSの核となるマンガンシリケート系酸
化物を構成する重要な元素であり、0.2%以下ではそ
の効果が期待できず、さらにSiは脱酸元素として0.
2%以上の添加が必要であり、1.2%を超えると脆化
をもたらし溶接接合性も減ずるので、0.20〜1.2
0%に限定した。Si not only contributes to the strengthening of the ferrite phase in the pearlite structure by solid solution hardening, but also contributes slightly to the improvement of the toughness of the rail steel. Further, Si is an important element that constitutes a manganese silicate-based oxide that becomes a core of MnS together with Mn, and if 0.2% or less, its effect cannot be expected, and Si is a deoxidizing element of 0.1.
It is necessary to add 2% or more, and if it exceeds 1.2%, embrittlement is caused and weld bondability is reduced.
Limited to 0%.
【0008】MnはC同様にパーライト変態温度を低下
させ、焼入性を高めることによって高強度化に寄与する
元素であり、さらにSi同様にMnSの核としてのマン
ガンシリケートの構成元素として、および脱酸元素とし
ても欠かせない。しかし、0.5%未満ではその効果が
小さくまた1.50%を超えると偏析部にマルテンサイ
ト組織を生成させ易くするため0.50〜1.50%に
限定した。Like C, Mn is an element that contributes to the strengthening by lowering the pearlite transformation temperature and enhancing hardenability. Further, like Mn, it is a constituent element of manganese silicate as the core of MnS, and deoxidation. It is indispensable as an acid element. However, if it is less than 0.5%, its effect is small, and if it exceeds 1.50%, the content is limited to 0.50 to 1.50% so that a martensite structure is easily generated in the segregated portion.
【0009】Sは一般に有害元素として知られている
が、本発明においてはオーステナイト粒内のマンガンシ
リケートなどの酸化物を核とするMnSを基地とする析
出物(VC)が生成し、これを変態核とするパーライト
組織が生成するため欠かせない元素である。しかし、
0.006%未満ではパーライト変態核としてのMnS
量が減じてしまい、パーライト粒内変態を確保できなく
する。また0.035%以上ではMnSが多量に生成し
靭性を著しく低下させるため0.006〜0.035%
に限定した。Although S is generally known as a harmful element, in the present invention, a precipitate (VC) based on MnS having an oxide such as manganese silicate in austenite grains as a nucleus is formed and transformed. It is an essential element because it produces a pearlite structure as the nucleus. But,
If less than 0.006%, MnS as pearlite transformation nuclei
The amount decreases, and it becomes impossible to secure the pearlite intragranular transformation. If it is more than 0.035%, a large amount of MnS is formed and the toughness is remarkably lowered, so 0.006 to 0.035%.
Limited to.
【0010】Crは、パーライト変態を低下させること
によって高強度化に寄与すると同時に、パーライト組織
中のセメンタイト相を強化することによっても耐摩耗性
向上に貢献するが、一方ではセメンタイトの衝撃靭性を
低下させる作用も有している。しかし、Crのセメンタ
イト強化作用は無視しがたく、さらに溶接継ぎ手部軟化
防止の観点からも微量のCrの添加も望ましい。そこで
強度確保に一定の寄与が期待されかつ靭性を損なわない
範囲内で0.1〜1.0%に限定した。[0010] Cr contributes to the increase in strength by lowering the pearlite transformation, and at the same time contributes to the improvement of wear resistance by strengthening the cementite phase in the pearlite structure. On the other hand, it reduces the impact toughness of cementite. It also has the effect of causing it. However, the cementite strengthening effect of Cr cannot be ignored, and addition of a small amount of Cr is also desirable from the viewpoint of preventing softening of the welded joint. Therefore, it is limited to 0.1 to 1.0% within a range in which a certain contribution is expected to ensure strength and the toughness is not impaired.
【0011】Vは本発明の重要な構成要素であるが、冷
却中にMnS上に析出させたV炭化物を核としたパーラ
イト変態の生成を見いだしたことにより、従来オーステ
ナイト粒界に限定されていたパーライト変態核がオース
テナイト粒内からも期待でき、結果として微細なパーラ
イト粒からなるレール鋼を得ることができるようになり
大幅な靭性の向上を果たすことができた。しかし、0.
01%未満では、この効果が弱く、また1.0%以上添
加するとV炭化物が粗大化し、レール頭部内部からの疲
労き裂発生起点となることから、V添加量を0.01〜
1.0%の範囲に限定した。不可避的不純物元素である
Pは、レール鋼の靭性を向上させるためにはできるだけ
低減させることが望ましい。Although V is an important constituent of the present invention, it has been conventionally limited to austenite grain boundaries by the formation of pearlite transformation centered on V carbide precipitated on MnS during cooling. The pearlite transformation nuclei can be expected also from within the austenite grains, and as a result, a rail steel composed of fine pearlite grains can be obtained, and the toughness can be significantly improved. However, 0.
If it is less than 01%, this effect is weak, and if it is added in an amount of 1.0% or more, V carbides are coarsened and become a starting point of fatigue crack initiation from inside the rail head.
It was limited to the range of 1.0%. It is desirable to reduce P, which is an unavoidable impurity element, as much as possible in order to improve the toughness of the rail steel.
【0012】前記のような成分組成で構成されるレール
鋼は、転炉、電気炉などの通常使用される溶解炉で前述
した脱酸を含む溶製を行い、この溶鋼を造塊・分塊法あ
るいは連続鋳造法、さらに熱間圧延を経て製造する。熱
間圧延を終えたレールは、冷却中においてオーステナイ
ト粒内のMnSに析出したV炭化物からもパーライト変
態が生成し、オーステナイト粒界から生成するパーライ
トと共に微細なパーライト粒を構成する。その結果、圧
延ままで靭性の優れた高強度レールを製造することがで
きる。The rail steel having the above-mentioned composition of components is melted by the above-mentioned deoxidizing process in a commonly used melting furnace such as a converter or an electric furnace, and this molten steel is ingoted or agglomerated. Method or continuous casting method, and then hot rolling. The rails that have undergone hot rolling also undergo pearlite transformation from V carbides precipitated in MnS in austenite grains during cooling, and form fine pearlite grains together with pearlite produced from austenite grain boundaries. As a result, a high-strength rail having excellent toughness can be manufactured as rolled.
【0013】さらに高強度とともに高靭性が要求される
場合には、圧延終了後あるいは、一度室温に冷却され熱
処理する目的で再加熱されたオーステナイト域温度から
冷却する際に、700〜500℃間を1〜5℃/secで加
速冷却されたレール鋼では、一層の高靭性が得られる。
すなわち、パーライト組織鋼の特徴として、加速冷却す
ることによって低温でパーライト変態を生じさせ、この
ことによりパーライト変態核の生成速度が向上し結果的
にパーライト粒を微細にすることができるからである。
従ってMnS上に析出させたV炭化物からのパーライト
組織のオーステナイト粒内変態と、加速冷却によるオー
ステナイト粒界からのパーライト変態が重畳して一層の
レール鋼の靭性向上を達成することができる。この際冷
却媒体は、空気あるいはミストなどの気液混合物を用
い、レール頭部もしくは底部の強度が1100MPa 以上
とすることが望ましい。When high strength and high toughness are required, a temperature of 700 to 500 ° C. is set after completion of rolling or when cooling from the austenite region temperature reheated once for the purpose of heat treatment after cooling to room temperature. Rail steels that have been accelerated cooled at 1 to 5 ° C / sec can achieve even higher toughness.
That is, as a characteristic of the pearlite structure steel, pearlite transformation is caused at a low temperature by accelerated cooling, whereby the generation rate of pearlite transformation nuclei is improved, and as a result, pearlite grains can be made fine.
Therefore, the austenite intragranular transformation of the pearlite structure from the V carbides precipitated on MnS and the pearlite transformation from the austenite grain boundaries due to accelerated cooling can be superimposed to further improve the toughness of the rail steel. At this time, it is desirable that the cooling medium is a gas-liquid mixture such as air or mist, and the strength of the rail head or bottom is 1100 MPa or more.
【0014】レール鋼の靭性評価法としては、ロシアの
GOST規格によって定められた2mmUノッチシャルピ
ー試験における+20℃での衝撃吸収エネルギーがあ
り、同規格によれば高強度熱処理レールの+20℃での
衝撃吸収エネルギーは0.25MJ/m2 以上が必要とされ
ている。上述したオーステナイト粒内のMnSに析出さ
せたV炭化物をパーライト変態核として活用することに
よって、本発明のレール鋼ではパーライト粒が微細化
し、0.25MJ/m2 以上の衝撃吸収エネルギーを得るこ
とができる。As a method for evaluating the toughness of rail steel, there is the impact absorbed energy at + 20 ° C. in the 2 mm U-notch Charpy test defined by the Russian GOST standard. According to this standard, the impact of the high-strength heat-treated rail at + 20 ° C. Absorbed energy is required to be 0.25 MJ / m 2 or more. By utilizing the above-mentioned V carbides precipitated in MnS in the austenite grains as pearlite transformation nuclei, the pearlite grains are refined in the rail steel of the present invention, and impact absorption energy of 0.25 MJ / m 2 or more can be obtained. it can.
【0015】[0015]
【実施例】次に本発明により製造した高靭性を有する高
強度レールの製造実施例について述べる。表1は供試鋼
の化学成分およびV添加、無添加鋼のそれぞれ冷却後の
組織中にMnSを核とするパーライト粒内変態が含まれ
ているかどうかを観察した結果を示す。また、表2には
圧延まま、および強度を一定とするために化学成分ごと
に700〜500℃間を冷却速度1〜5℃/secの範囲で
変化させた加速冷却後のレール鋼の引張試験強度および
2mmUノッチシャルピー試験における+20℃での衝撃
吸収エネルギー測定結果を示す。EXAMPLES Next, examples of production of high strength rails having high toughness produced according to the present invention will be described. Table 1 shows the results of observing whether the chemical composition of the sample steel and whether or not the V-added steel and the V-free steel each contain pearlite intragranular transformation having MnS as a nucleus in the microstructure after cooling. In addition, Table 2 shows the tensile test of the rail steel as it is rolled and after accelerated cooling in which the cooling rate is changed between 700 and 500 ° C for each chemical component in the range of the cooling rate of 1 to 5 ° C / sec in order to keep the strength constant. The results of strength and impact absorbed energy measurement at + 20 ° C. in a 2 mm U-notch Charpy test are shown.
【0016】衝撃試験片はレール頭部1mm下より採取し
た。この試験条件は熱処理レールにおける靭性を規定し
たロシアのGOST規格に基づくもので、同規格によれ
ば高強度熱処理レールの+20℃での衝撃吸収エネルギ
ーは0.25MJ/m2 以上が必要とされており、本発明の
オーステナイト粒内からもパーライト変態を生成させた
微細パーライト組織鋼は、いずれもGOST規格に定め
られたシャルピー吸収エネルギーを十分に満たしてい
る。The impact test piece was taken from 1 mm below the rail head. This test condition is based on the Russian GOST standard that regulates the toughness of heat treated rails. According to this standard, the impact absorption energy at + 20 ° C of high strength heat treated rails must be 0.25 MJ / m 2 or more. Therefore, the fine pearlite structure steels in which the pearlite transformation is generated from the austenite grains of the present invention all sufficiently satisfy the Charpy absorbed energy defined in the GOST standard.
【0017】[0017]
【表1】 [Table 1]
【0018】[0018]
【表2】 [Table 2]
【0019】[0019]
【発明の効果】以上説明したように本発明によれば、オ
ーステナイト粒界のみならず、粒内からもパーライトを
微細に生成させて、圧延ままでも優れた靭性を有し寒冷
地でも安全な高強度レールを提供できる。As described above, according to the present invention, pearlite is finely generated not only from the austenite grain boundaries but also from inside the grain, and it has excellent toughness even in the as-rolled state and is safe in cold regions. Can provide strength rails.
【図1】V添加有無によるレールのGOST規格に定め
られたシャルピー衝撃値を示す図。FIG. 1 is a diagram showing a Charpy impact value defined by a GOST standard of a rail with or without addition of V.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 若生 昌光 千葉県富津市新富20−1 新日本製鐵株式 会社技術開発本部内 (72)発明者 船木 秀一 千葉県富津市新富20−1 新日本製鐵株式 会社技術開発本部内 ─────────────────────────────────────────────────── ─── Continuation of front page (72) Inventor Masamitsu Waka 20-1 Shintomi, Futtsu-shi, Chiba Shin Nippon Steel Co., Ltd.Technology Development Headquarters (72) Inventor Shuichi Funaki 20-1 Shintomi, Futtsu-shi, Chiba New Japan Iron & Steel Co., Ltd.
Claims (2)
つ、オーステナイト粒内のMnSを核としたパーライト
が存在することを特徴とする靭性に優れた高強度レー
ル。1. By weight%, C: 0.55 to 0.85% Si: 0.20 to 1.20% Mn: 0.50 to 1.50% S: 0.006 to 0.035% Cr: 0.1 to 1.0% V: 0.01 to 1.0%, the balance consisting of iron and unavoidable impurities, and the presence of pearlite having MnS as a nucleus in austenite grains. High strength rail with excellent toughness.
熱間圧延終了後、あるいは熱処理する目的で高温に加熱
した後、レールの頭部あるいはさらに底部を、オーステ
ナイト域温度から冷却する際に700〜500℃間を1
〜5℃/secで加速冷却し、オーステナイト粒内のMnS
を核としたパーライトが生成させることを特徴とする靭
性に優れた高強度レールの製造法。2. By weight%, C: 0.55 to 0.85% Si: 0.20 to 1.20% Mn: 0.50 to 1.50% S: 0.006 to 0.035% Cr: 0.1 to 1.0% V: 0.01 to 1.0% is contained, and the balance is steel and iron and inevitable impurities. After hot rolling is completed, or after heating to a high temperature for the purpose of heat treatment, When cooling the head or the bottom of the rail from the austenitic temperature, the temperature must be between 700 and 500 ° C for 1
Accelerated cooling at ~ 5 ° C / sec, MnS in austenite grains
A method for producing a high-strength rail with excellent toughness, which is characterized by generating pearlite with a core of.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP5261193A JPH06340951A (en) | 1993-03-12 | 1993-03-12 | High strength rail excellent in toughness and its production |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP5261193A JPH06340951A (en) | 1993-03-12 | 1993-03-12 | High strength rail excellent in toughness and its production |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH06340951A true JPH06340951A (en) | 1994-12-13 |
Family
ID=12919600
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP5261193A Pending JPH06340951A (en) | 1993-03-12 | 1993-03-12 | High strength rail excellent in toughness and its production |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH06340951A (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2785890B1 (en) | 2011-11-28 | 2015-07-15 | Tata Steel UK Ltd | Rail steel with an excellent combination of wear properties, rolling contact fatigue resistance and weldability |
EP2006406A4 (en) * | 2006-03-16 | 2015-08-12 | Jfe Steel Corp | High-strength pearlite rail with excellent delayed-fracture resistance |
WO2016027467A1 (en) * | 2014-08-20 | 2016-02-25 | Jfeスチール株式会社 | Heat treatment rail manufacturing method and manufacturing apparatus |
CN113699452A (en) * | 2021-08-30 | 2021-11-26 | 宝武集团马钢轨交材料科技有限公司 | Steel for tramcar elastic wheel rim and heat treatment method and production method thereof |
-
1993
- 1993-03-12 JP JP5261193A patent/JPH06340951A/en active Pending
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2006406A4 (en) * | 2006-03-16 | 2015-08-12 | Jfe Steel Corp | High-strength pearlite rail with excellent delayed-fracture resistance |
EP2785890B1 (en) | 2011-11-28 | 2015-07-15 | Tata Steel UK Ltd | Rail steel with an excellent combination of wear properties, rolling contact fatigue resistance and weldability |
WO2016027467A1 (en) * | 2014-08-20 | 2016-02-25 | Jfeスチール株式会社 | Heat treatment rail manufacturing method and manufacturing apparatus |
JPWO2016027467A1 (en) * | 2014-08-20 | 2017-04-27 | Jfeスチール株式会社 | Heat treatment rail manufacturing method and manufacturing apparatus |
US10472693B2 (en) | 2014-08-20 | 2019-11-12 | Jfe Steel Corporation | Head hardened rail manufacturing method and manufacturing apparatus |
CN113699452A (en) * | 2021-08-30 | 2021-11-26 | 宝武集团马钢轨交材料科技有限公司 | Steel for tramcar elastic wheel rim and heat treatment method and production method thereof |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP2009041079A (en) | Steel for welded structure having excellent toughness in weld heat-affected zone, method for producing the same, and method for producing welded structure | |
JPH06100923A (en) | Production of oxide-containing fire resistant shape steel by controlled rolling | |
JPH07278656A (en) | Production of low yield ratio high tensile strength steel | |
JP3267772B2 (en) | Manufacturing method of high strength, high ductility, high toughness rail | |
JPH06279928A (en) | High strength rail excellent in toughness and ductility and its production | |
JPS613842A (en) | Manufacture of high strength rail | |
JPH09206804A (en) | Manufacture of high-strength rail excellent in ductility and toughness | |
JPH0541683B2 (en) | ||
JPH06279927A (en) | High strength rail excellent in ductility and toughness and its production | |
JPH06128631A (en) | Production of high manganese ultrahigh tensile strength steel excellent in low temperature toughness | |
JPH06340951A (en) | High strength rail excellent in toughness and its production | |
JP2001003140A (en) | High strength pearlitic rail excellent in toughness and ductility and its production | |
JPH0693332A (en) | Production of high tensile strength and high toughness fine bainitic steel | |
JP3117916B2 (en) | Manufacturing method of pearlitic rail with excellent wear resistance | |
JP3368557B2 (en) | High strength rail with excellent ductility and toughness and its manufacturing method | |
JP3323272B2 (en) | Manufacturing method of high strength rail with excellent ductility and toughness | |
JP3117915B2 (en) | Manufacturing method of high wear resistant pearlite rail | |
JPH0718326A (en) | Production of highly strong and tough rail by on-line heat treatment | |
JPH05148544A (en) | Production of high-strength high-toughness steel plate having uniform hardness distribution in thickness direction | |
JP2000328190A (en) | High strength pearlitic rail excellent in toughness and ductility and its production | |
JPH0143005B2 (en) | ||
JPH09227943A (en) | Production of high strength rail excellent in ductility and toughness | |
JPH07126741A (en) | Production of high ductility and high toughness rail | |
JPH0967620A (en) | Production of heat treated type high tensile strength steel plate excellent in brittle crack arrest property | |
JP2543282B2 (en) | Method for producing controlled rolled steel with excellent toughness |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
A02 | Decision of refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A02 Effective date: 20011106 |