JPH10219386A - Steele for structural purpose excellent in strength and toughness - Google Patents
Steele for structural purpose excellent in strength and toughnessInfo
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- JPH10219386A JPH10219386A JP3439697A JP3439697A JPH10219386A JP H10219386 A JPH10219386 A JP H10219386A JP 3439697 A JP3439697 A JP 3439697A JP 3439697 A JP3439697 A JP 3439697A JP H10219386 A JPH10219386 A JP H10219386A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は強度および靱性に優
れた構造用鋼に係り、特にＢを含有する強度および靱性
に優れた熱間圧延鋼材又は熱処理鋼材に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a structural steel having excellent strength and toughness, and more particularly to a hot-rolled steel or a heat-treated steel containing B and having excellent strength and toughness.
【０００２】[0002]
【従来の技術】従来、土木、建築、橋梁、船舶、車両、
石油貯蔵、容器その他の構造物に使用される鋼材は、鉄
鋼ＪＩＳ３１０６、３１３６などに規定されているＣ、
Ｓｉ、Ｍｎを主成分とする熱間圧延鋼材が多用される。
組織的にはこの種の鋼材はフェライト相を主たる構成相
とし、これにパーライトさらにはベーナイト、マルテン
サイトなどの高強度の低温変態相から成り立っている。
しかしながらこれらの低温変態相は一般に靱性が低いた
めに、これらの鋼材は構造用鋼として必須の特性である
強度と靱性を兼備させることが課題となっていた。2. Description of the Related Art Conventionally, civil engineering, architecture, bridges, ships, vehicles,
Steel materials used for oil storage, containers and other structures are specified by C, specified in steel JIS3106, 3136, etc.
A hot rolled steel material containing Si and Mn as main components is often used.
In terms of structure, this kind of steel material mainly comprises a ferrite phase, and further comprises a pearlite and a high-strength low-temperature transformation phase such as bainite and martensite.
However, since these low-temperature transformation phases generally have low toughness, it has been an issue for these steel materials to have both strength and toughness, which are essential properties for structural steel.
【０００３】この課題を解決するため、日本金属学会
報、第２７巻第８号（１９８８）６２３ページに示され
ているように圧延過程における熱履歴等を制御してオー
ステナイト粒内に微細なフェライト粒を析出させるとと
もに、低温変態相の分断、微細化を図り、強度と靱性を
ともに確保する手段が提案されており、相当の成果を挙
げている。しかしながら、この手法は必ずしも全ての鋼
材に適用できず、またその実施には大規模な製造設備を
必要とし、また圧延条件の厳しい規制のために圧延材に
形状不良が発生する場合があるなどの問題があった。[0003] In order to solve this problem, as shown in the Japan Institute of Metals, Vol. 27, No. 8 (1988), p. Means for precipitating grains, separating and refining the low-temperature transformation phase, and securing both strength and toughness have been proposed, and have achieved considerable results. However, this method is not always applicable to all steel materials, and its implementation requires large-scale manufacturing equipment, and strict regulations on rolling conditions may cause rolled materials to have defective shapes. There was a problem.
【０００４】一方、たとえば、新日鐵技法第３５１号
（１９９３）６４ページ以下に記載されているように鋼
中に酸化物などの介在物、析出物を分散させ、それらを
核としてオーステナイト粒内に微細なフェライト粒を析
出させる手段も提案されている。しかしこの手法では介
在物や析出物の析出条件が鋼の組成や製造条件に敏感で
あるため、適量の介在物などを適時に析出させることが
困難である。On the other hand, for example, as described in Nippon Steel Technology No. 351 (1993), p. 64 et seq., Inclusions such as oxides and precipitates are dispersed in steel, and these are used as nuclei to form austenite grains. Means for precipitating fine ferrite grains have also been proposed. However, in this method, the precipitation conditions of inclusions and precipitates are sensitive to the composition of the steel and the production conditions, so that it is difficult to precipitate an appropriate amount of inclusions and the like in a timely manner.
【０００５】[0005]
【発明が解決しようとする課題】本発明は、上記従来技
術の有する問題点を解決し、強度と靱性を兼備した構造
用鋼材を提供することを目的とするものである。具体的
には、いわゆる５０ｋｇクラスの高張力鋼（引張強さ５
１０ないし５５０ＭＰａ）においてシャルピー衝撃試験
の吸収エネルギーが２００Ｊ以上である新たな組成の構
造用鋼を提供することを目的とするものである。また本
発明は新たなフェライト生成核を提案し、これにより強
度と靭性を兼備した構造用鋼材を幅広い鋼種にわたっ
て、形状不良を発生することなく、かつフェライト核生
成量の制御可能な状態で製造可能とするものである。SUMMARY OF THE INVENTION An object of the present invention is to solve the above-mentioned problems of the prior art and to provide a structural steel material having both strength and toughness. Specifically, a so-called 50 kg class high-strength steel (tensile strength 5
It is an object of the present invention to provide a structural steel having a new composition having an absorption energy of 200 J or more in a Charpy impact test at 10 to 550 MPa). In addition, the present invention proposes a new ferrite nucleation nucleus, which makes it possible to manufacture structural steel materials having both strength and toughness over a wide range of steel types without causing shape defects and with controllable ferrite nucleation amount. It is assumed that.
【０００６】[0006]
【課題を解決するための手段】上記課題の解決のため本
発明者らは、高ボロン鋼で晶出するＦｅ2Ｂがフェライ
ト核生成サイトとして優れた能力のあることを発見し、
本発明を完成させたものである。すなわち、本発明は鋼
の組成を以下のように規定することによって、鋳造時、
樹枝状晶間に晶出し、その後の圧延過程で分断、微細化
されるＦｅ2Ｂをオーステナイト粒内におけるフェライ
ト相の生成サイトとして利用するとともに、固溶Ｂを利
用してオーステナイト粒界におけるフェライト相の生成
を抑制し、強度と靭性を具備した構造用鋼の製造を可能
にしたものである。Means for Solving the Problems To solve the above problems, the present inventors have found that Fe 2 B crystallized from high boron steel has excellent ability as a ferrite nucleation site,
The present invention has been completed. That is, the present invention defines the composition of steel as follows, at the time of casting,
The Fe 2 B crystallized between the dendrites and separated and refined in the subsequent rolling process is used as a site for forming a ferrite phase in the austenite grains, and the ferrite phase at the austenite grain boundary is utilized using solid solution B. The production of structural steel having strength and toughness is suppressed by suppressing the formation of steel.
【０００７】具体的には、強度および靱性に優れた構造
用鋼の組成を、質量比で、Ｃ：０．０３％以上、０．２
４％以下、Ｓｉ：１．０％以下、Ｍｎ：２．０％以下、
Ｐ：０．０１％以下、Ｓ：０．０１％以下、Ｎ：０．０
０５％以下、Ｂ：０．０２０％以上、０．５００％以
下、を含有し、残部鉄および不可避不純物からなるもの
とするものである。さらに、上記組成に加え、Ｎｉ：
１．４％以下、Ｃｒ：０．９％以下、Ｍｏ：０．５％以
下、Ｖ：０．３％以下、Ｎｂ：０．３％以下、Ｔｉ：
０．３％以下、Ｚｒ：０．１％以下から選んだ１種又は
２種以上を必要に応じ選択的に含有せしめるものであ
る。[0007] Specifically, the composition of structural steel having excellent strength and toughness is defined as a mass ratio of C: 0.03% or more, 0.2% or more.
4% or less, Si: 1.0% or less, Mn: 2.0% or less,
P: 0.01% or less, S: 0.01% or less, N: 0.0
B: 0.05% or less, B: 0.020% or more and 0.500% or less, with the balance being iron and unavoidable impurities. Further, in addition to the above composition, Ni:
1.4% or less, Cr: 0.9% or less, Mo: 0.5% or less, V: 0.3% or less, Nb: 0.3% or less, Ti:
One or more selected from 0.3% or less and Zr: 0.1% or less are selectively contained as necessary.
【０００８】[0008]
【発明の実施の形態】まず本発明の構造用鋼の組成につ
いて説明する。 Ｃ：０．０３％以上、０．２４％以下 Ｃはオーステナイト相からの低温変態相の種類、量を決
定するので、０．０３％以上を添加して鋼材の強度を確
保する。しかし、過剰に添加すると高温フェライト相の
生成が抑制され、Ｆｅ2Ｂの効果が期待出来なくなる。
したがって、その上限は０．２４％とした。DESCRIPTION OF THE PREFERRED EMBODIMENTS First, the composition of the structural steel of the present invention will be described. C: 0.03% or more, 0.24% or less C determines the type and amount of the low-temperature transformation phase from the austenite phase. Therefore, 0.03% or more is added to secure the strength of the steel material. However, if added excessively, the formation of a high-temperature ferrite phase is suppressed, and the effect of Fe 2 B cannot be expected.
Therefore, the upper limit is set to 0.24%.
【０００９】Ｓｉ：１．０％以下、Ｍｎ：２．０％以下 Ｓｉは脱酸剤として、又鋼の焼入性の調整剤として低温
変態相の分率の調整に重要な元素であり、必須の添加元
素である。しかし、１．０％を越えると鋼を脆化させる
ため、その添加量は１．０％以下とする。ＭｎはＳを無
害化し、靭性を向上させるほか、鋼の焼入性の調整、低
温変態相の生成分率の調整のため必須の添加元素であ
る。しかし、２．０％以上添加すると鋼を脆化させるの
で、上限を２．０％とした。Si: 1.0% or less, Mn: 2.0% or less Si is an important element for adjusting the fraction of the low-temperature transformation phase as a deoxidizing agent and as a modifier for the hardenability of steel. It is an essential additive element. However, if it exceeds 1.0%, the steel is embrittled, so the amount of addition is limited to 1.0% or less. Mn is an indispensable additive element for detoxifying S, improving toughness, adjusting the hardenability of steel, and adjusting the generation fraction of the low-temperature transformation phase. However, if 2.0% or more is added, the steel is embrittled, so the upper limit is set to 2.0%.
【００１０】Ｂ：０．０２０％以上、０．５００％以下 Ｂは初晶としてＦｅ2Ｂを生成し、それがその後の熱間
加工によって分断、微細化され、オーステナイト相中に
分散し、フェライト相の生成核として作用する。また、
オーステナイト相中からＦｅ2Ｂを析出し、同様にフェ
ライト相の生成核となる。一方、Ｆｅ2Ｂの生成に寄与
しないＢは固溶Ｂとしてオーステナイト結晶粒界に偏析
し粒界フェライトの生成を抑制し、オーステナイト粒内
におけるフェライト相の生成に寄与する。したがって、
Ｂは本発明において必須の添加元素である。その効果は
０．０２０％以上で現れるが、過剰に添加する場合はフ
ェライト相の生成に寄与しないＦｅ2Ｂが硬質の介在物
相として鋼の加工性や靭性を劣化させるため０．５００
％以下としなければならない。なお、Ｂの鋼中への固溶
度は極めて小さいので、鋼中に添加されるＢはほぼすべ
てＦｅ2Ｂを生成すると考えてよく、したがってフェラ
イト相生成核の存在量をＢの添加量のみに化学量論的に
決定できることになる。B: 0.020% or more and 0.500% or less B forms Fe 2 B as a primary crystal, which is divided and refined by the subsequent hot working, dispersed in the austenite phase, and ferrite. Acts as a phase nucleus. Also,
Fe 2 B is precipitated from the austenite phase, and also serves as a nucleus for forming a ferrite phase. On the other hand, B that does not contribute to the formation of Fe 2 B segregates at the austenite crystal grain boundary as solid solution B, suppresses the formation of grain boundary ferrite, and contributes to the formation of a ferrite phase in austenite grains. Therefore,
B is an essential additive element in the present invention. The effect appears at 0.020% or more. However, when added in excess, Fe 2 B, which does not contribute to the formation of a ferrite phase, deteriorates the workability and toughness of the steel as a hard inclusion phase, so that 0.500% or more.
% Or less. Since the solid solubility of B in steel is extremely small, it can be considered that almost all of B added to steel forms Fe 2 B. Therefore, the abundance of ferrite phase nuclei is determined only by the amount of B added. Can be determined stoichiometrically.
【００１１】Ｐ：０．０１％以下、Ｓ：０．０１％以
下、Ｎ：０．００５％以下 Ｐ、Ｓはともに粒界偏析により構造用鋼にとって重要な
特性値である靭性を低下させるほか、Ｂの粒界偏析と競
合し、その効果を低減させる。したがってこれらは０．
０１％以下に制限しなければならない。また、Ｎは粒界
に偏析し、Ｂと反応してＢＮを形成し、粒界Ｂの効果を
低減させる。したがって、０．００５％以下に制限され
なければならない。P: 0.01% or less, S: 0.01% or less, N: 0.005% or less Both P and S reduce toughness which is an important characteristic value for structural steel due to grain boundary segregation. , B compete with the grain boundary segregation and reduce its effect. Therefore, these are 0.
Must be limited to 01% or less. N segregates at the grain boundaries and reacts with B to form BN, thereby reducing the effect of the grain boundaries B. Therefore, it must be limited to 0.005% or less.
【００１２】Ｎｉ、Ｃｒ、Ｍｏ、Ｖ、Ｎｂ、Ｔｉ、Ｚｒ
は何れも焼入性を向上させる元素であり、低温変態相の
分率の調整等の目的で適宜添加することが出来る。しか
し過剰に添加してもその効果が飽和するのみでなく、か
えって鋼の脆化を招く。従って、これら元素はそれぞれ
１．４％、０．９％、０．５％、０．３％、０．３％、
０．３％、０．１％を上限として１種または２種以上を
必要に応じ選択的に添加することとする。Ni, Cr, Mo, V, Nb, Ti, Zr
Are elements that improve the hardenability, and can be appropriately added for the purpose of adjusting the fraction of the low-temperature transformation phase. However, even if it is added excessively, not only the effect is saturated, but also the steel becomes brittle. Therefore, these elements are 1.4%, 0.9%, 0.5%, 0.3%, 0.3%,
One or two or more kinds are selectively added as necessary, with the upper limit being 0.3% or 0.1%.
【００１３】本発明鋼の組織は、フェライト相と炭化物
を含む第二相とからなる。これらの相の存在割合は本発
明の構造用鋼に要求される強度、靭性などによって適宜
決定すればよいが、オーステナイト相からＦｅ2Ｂを核
として析出するいわゆる粒内フェライトの分率を１０な
いし６０％とするのが強度と靭性とのバランス上好まし
い。かかるフェライト分率を得るために前述のようにＢ
添加が行われるが、その添加量はＣ、Ｍｎ等の低温変態
相生成促進元素の量、熱延条件など鋼の製造条件によっ
て定められる。The structure of the steel according to the present invention comprises a ferrite phase and a second phase containing carbide. The proportion of these phases may be appropriately determined depending on the strength and toughness required for the structural steel of the present invention. The fraction of so-called intragranular ferrite which precipitates from the austenitic phase with Fe 2 B as a nucleus is 10 to 10%. It is preferable to be 60% in terms of balance between strength and toughness. To obtain such a ferrite fraction, B
The addition is performed, and the amount of addition is determined by the amount of the element for promoting the formation of the low-temperature transformation phase such as C and Mn, and the steel production conditions such as hot rolling conditions.
【００１４】[0014]
【実施例】以下、本発明の実施例を比較例と対比して示
す。表１に示す鋼を溶製し、連続鋳造法によってスラブ
を得、１１００℃に加熱後、板厚２０ｍｍの厚鋼板に熱
間圧延をした後、空冷し熱延板を得た。表１において鋼
ＡないしＤは本発明に規定する組成を有する鋼である
が、ＥないしＪは本発明の範囲を逸脱する鋼である。す
なわち、鋼Ｅ、ＦはＢを含有せず、鋼Ｇ、Ｈはそれぞれ
Ｃ含有量が本発明の範囲より低すぎ、あるいは高すぎる
鋼である。鋼ＨＪはそれぞれＭｎ、Ｎ含有量が高すぎる
鋼である。EXAMPLES Examples of the present invention will be shown below in comparison with comparative examples. A steel shown in Table 1 was melted, a slab was obtained by a continuous casting method, heated to 1100 ° C., hot-rolled to a thick steel plate having a thickness of 20 mm, and air-cooled to obtain a hot-rolled plate. In Table 1, steels A to D are steels having the composition specified in the present invention, while E to J are steels which deviate from the scope of the present invention. That is, steels E and F do not contain B, and steels G and H are steels each having a C content that is too low or too high in the range of the present invention. Steel HJ is a steel having too high Mn and N contents, respectively.
【００１５】上記により得た熱延ままの状態の熱延板か
ら引張試験片（ＪＩＳ５号：板状引張試験片）ならびに
シャルピー試験片（ＪＩＳ４号：Ｖノッチフルサイズ、
サイドノッチ、Ｌ方向）を切り出し、ＪＩＳ Ｚ ２２
４１ならびにＪＩＳ Ｚ ２２４２に準拠して室温の引
張破断試験ならびに０℃の衝撃試験を実施した。また粒
内フェライト相分率も評価した。ここにに粒内フェライ
ト相分率とは旧オーステナイト粒界から生成したフェラ
イト相の分率をいう。From the hot-rolled sheet obtained as described above, a tensile test piece (JIS No. 5: plate-like tensile test piece) and a Charpy test piece (JIS No. 4: V notch full size)
Cut out side notch, L direction), JIS Z22
A room temperature tensile break test and an impact test at 0 ° C. were performed in accordance with No. 41 and JIS Z 2242. The intragranular ferrite fraction was also evaluated. Here, the intragranular ferrite phase fraction refers to the fraction of the ferrite phase generated from the prior austenite grain boundaries.
【００１６】上記試験によって得られた強度、靱性なら
びに粒内フェライト相分率の値を表１に併せて示す。本
発明の鋼組成を有するＡないしＤ鋼は３０ないし４０％
の適度の粒内フェライト相分率を有しそれにより優れた
強度および靱性を有するが、Ｅ、Ｆ、Ｉ、Ｊ鋼の粒内フ
ェライト相分率は著しく低く（高々１０％）、そのため
靱性において劣っている。すなわち、Ｂを含有しないＥ
鋼、Ｆ鋼は粒内フェライト相が形成されず、そのため強
度は確保されるものの靱性値が著しく低く構造用部材と
して適さない。Ｉ鋼はＭｎが高すぎ、いわゆる焼き入れ
性が高すぎるため、Ｂ含有量の条件は満たしてもＦｅ2
Ｂによるフェライト相生成効果は発揮されず、強度が著
しく高く靱性の低いものとなり構造用鋼として適さな
い。Ｊ鋼はＮが高すぎるため粒界に偏析したＢがＮと結
合してＢＮを形成し粒界フェライトを生成しやすくする
ために、十分な粒内フェライト相の形成が行われず靱性
が低い。Ｇ鋼はＢは添加されているもののＣ量が低すぎ
るため硬質相の形成が行われず、そのため構造用鋼とし
て必要な強度が得られない。またＨ鋼はＣが高すぎるた
め、Ｂが十分添加されていても硬質相の量が多くなりす
ぎ強度が著しく高くて靱性が低く、やはり構造用部材に
用いるには不適当である。The values of the strength, toughness and intragranular ferrite phase fraction obtained by the above test are also shown in Table 1. A to D steel having the steel composition of the present invention is 30 to 40%
Has a moderate intragranular ferrite phase fraction and thus has excellent strength and toughness, but the E, F, I, and J steels have a significantly low intragranular ferrite phase fraction (at most 10%), so that Inferior. That is, E not containing B
Steel and F steel do not have an intragranular ferrite phase, and therefore have high strength, but are extremely low in toughness and are not suitable as structural members. Steel I has too high Mn, so-called hardenability, so that even if the B content condition is satisfied, Fe 2
The effect of ferrite phase formation by B is not exhibited, and the strength is extremely high and the toughness is low, so that the steel is not suitable as a structural steel. J steel has too high N, so that B segregated at the grain boundary is combined with N to form BN to easily generate intergranular ferrite, so that a sufficient intragranular ferrite phase is not formed and the toughness is low. In steel G, although B is added, the amount of carbon is too low to form a hard phase, so that the strength required for structural steel cannot be obtained. In addition, since H steel has too high C, even if B is sufficiently added, the amount of the hard phase is too large, the strength is remarkably high, and the toughness is low, which is also unsuitable for use as a structural member.
【００１７】[0017]
【表１】 [Table 1]
【００１８】なお、Ａ鋼は請求項１に該当する例であ
り、一方Ｂ鋼ないしＤ鋼はＮｉ、Ｃｒなどの合金元素を
選択的に含む請求項２に該当する例であり、これらにお
いてもＢ含有の効果が現れ、十分な粒内フェライト相の
形成とそれによる強度−靱性バランスの優れた鋼の得ら
れることが実証されている。また、上記実施例では熱間
圧延ままの鋼についての特性値を示したが、熱延後必要
により熱処理を施しても本発明の効果が現れることはも
ちろんである。Steel A is an example corresponding to claim 1, while steels B to D are examples corresponding to claim 2, which selectively contains alloying elements such as Ni and Cr. It has been demonstrated that the effect of B content appears and that a steel having an excellent balance between strength and toughness due to formation of a sufficient intragranular ferrite phase can be obtained. Further, in the above embodiment, the characteristic values of the steel as hot rolled are shown. However, the effect of the present invention can be obviously obtained even if a heat treatment is performed as necessary after hot rolling.
【００１９】[0019]
【発明の効果】以上のように本発明の鋼組成により、構
造用鋼として極めて適切な強度、靱性を具備する鋼を、
特に大規模な製造設備を要することなく、またフェライ
ト相の析出サイトの量を極めて容易に制御して製造する
ことができる。As described above, according to the steel composition of the present invention, a steel having extremely suitable strength and toughness as a structural steel can be obtained.
In particular, the production can be performed without requiring a large-scale production facility, and extremely easily controlling the amount of precipitation sites of the ferrite phase.
Claims (2)
％以下、Ｓｉ：１．０％以下、Ｍｎ：２．０％以下、
Ｐ：０．０１％以下、Ｓ：０．０１％以下、Ｎ：０．０
０５％以下、Ｂ：０．０２０％以上、０．５００％以
下、を含有し、残部鉄および不可避不純物からなる強度
および靱性に優れた構造用鋼。1. A mass ratio of C: 0.03% or more, 0.24 or more.
% Or less, Si: 1.0% or less, Mn: 2.0% or less,
P: 0.01% or less, S: 0.01% or less, N: 0.0
Structural steel containing 0.05% or less and B: 0.020% or more and 0.500% or less, and is excellent in strength and toughness composed of the balance of iron and unavoidable impurities.
％以下、Ｓｉ：１．０％以下、Ｍｎ：２．０％以下、
Ｐ：０．０１％以下、Ｓ：０．０１％以下、Ｎ：０．０
０５％以下、Ｂ：０．０２０％以上、０．５００％以
下、を含有しさらにＮｉ：１．４％以下、Ｃｒ：０．９
％以下、Ｍｏ：０．５％以下、Ｖ：０．３％以下、Ｎ
ｂ：０．３％以下、Ｔｉ：０．３％以下、Ｚｒ：０．１
％以下から選んだ１種又は２種以上を含有し、残部鉄お
よび不可避不純物からなる強度および靱性に優れた構造
用鋼。2. A mass ratio of C: 0.03% or more, 0.24 or more.
% Or less, Si: 1.0% or less, Mn: 2.0% or less,
P: 0.01% or less, S: 0.01% or less, N: 0.0
B: 0.020% or more, 0.500% or less, Ni: 1.4% or less, Cr: 0.9%
%, Mo: 0.5% or less, V: 0.3% or less, N
b: 0.3% or less, Ti: 0.3% or less, Zr: 0.1
% Or more, selected from the group consisting of iron and unavoidable impurities and having excellent strength and toughness.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3439697A JPH10219386A (en) | 1997-02-03 | 1997-02-03 | Steele for structural purpose excellent in strength and toughness |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3439697A JPH10219386A (en) | 1997-02-03 | 1997-02-03 | Steele for structural purpose excellent in strength and toughness |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH10219386A true JPH10219386A (en) | 1998-08-18 |
Family
ID=12413034
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3439697A Pending JPH10219386A (en) | 1997-02-03 | 1997-02-03 | Steele for structural purpose excellent in strength and toughness |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH10219386A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101167388B1 (en) | 2010-02-26 | 2012-07-19 | 현대제철 주식회사 | Steel Marine, and method for producing the same |
| CN104630640A (en) * | 2015-01-15 | 2015-05-20 | 西安交通大学 | Liquid-zinc-corrosive-wear-resistant monolithic material and preparation method thereof |
-
1997
- 1997-02-03 JP JP3439697A patent/JPH10219386A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101167388B1 (en) | 2010-02-26 | 2012-07-19 | 현대제철 주식회사 | Steel Marine, and method for producing the same |
| CN104630640A (en) * | 2015-01-15 | 2015-05-20 | 西安交通大学 | Liquid-zinc-corrosive-wear-resistant monolithic material and preparation method thereof |
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