JPH05186882A - High strength structural member - Google Patents
High strength structural memberInfo
- Publication number
- JPH05186882A JPH05186882A JP326192A JP326192A JPH05186882A JP H05186882 A JPH05186882 A JP H05186882A JP 326192 A JP326192 A JP 326192A JP 326192 A JP326192 A JP 326192A JP H05186882 A JPH05186882 A JP H05186882A
- Authority
- JP
- Japan
- Prior art keywords
- structural member
- intermediate layer
- hard surface
- surface layer
- soft intermediate
- 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
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は高強度構造部材、特に、
金属製部材本体に、局部溶融合金化処理により形成され
る硬質表面層を設けた高強度構造部材に関する。FIELD OF THE INVENTION This invention relates to high strength structural members, especially
The present invention relates to a high-strength structural member in which a hard surface layer formed by local melting alloying treatment is provided on a metal member main body.
【０００２】[0002]
【従来の技術】従来、この種構造部材においては、硬質
表面層が部材本体に直接接合されている。2. Description of the Related Art Conventionally, in this type of structural member, a hard surface layer is directly bonded to the member body.
【０００３】[0003]
【発明が解決しようとする課題】局部溶融合金化処理に
よる硬質表面層は非常に高い硬さを有する反面、高脆性
であるため、繰返し応力を受けるような使用環境下では
亀裂を発生し易い。この場合、亀裂が硬質表面層内にと
どまっていれば強度上問題はないが、従来のように硬質
表面層と部材本体とが直接接合されていると、硬質表面
層の亀裂が部材本体に容易に伝播して構造部材の強度が
損われる、という問題を生じる。The hard surface layer formed by the local melting alloying treatment has a very high hardness, but is also highly brittle, so that cracks are likely to occur in a use environment where repeated stress is applied. In this case, if the crack remains in the hard surface layer, there is no problem in strength, but if the hard surface layer and the member body are directly bonded as in the conventional case, the crack of the hard surface layer is easy to the member body. And the strength of the structural member is impaired.
【０００４】本発明は前記に鑑み、硬質表面層に発生し
た亀裂の部材本体への伝播を抑制して高強度を維持する
ことができるようにした前記構造部材を提供することを
目的とする。In view of the above, it is an object of the present invention to provide the above-mentioned structural member capable of suppressing the propagation of cracks generated in the hard surface layer to the member body and maintaining high strength.
【０００５】[0005]
【課題を解決するための手段】本発明は、金属製部材本
体に、局部溶融合金化処理により形成される硬質表面層
を設けた高強度構造部材において、前記部材本体と硬質
表面層との間に、それらと一体で、且つ前記硬質表面層
よりも低硬度の軟質中間層を介在させたことを特徴とす
る。The present invention relates to a high-strength structural member comprising a metal member body provided with a hard surface layer formed by local melting alloying treatment, wherein the member body and the hard surface layer are provided between the member body and the hard surface layer. In addition, a soft intermediate layer which is integral with them and has a hardness lower than that of the hard surface layer is interposed.
【０００６】[0006]
【実施例】図１は局部溶融合金化処理を示す。この処理
に当っては、微細な球状金属間化合物を分散させた金属
製母材、例えばＡｌ合金製母材１を矢示方向へ移動さ
せ、その表面をオシレータ２より照射されるレーザビー
ム３により溶融すると共にその溶融池４に粉末供給機５
よりキャリヤガスによって硬質化合金粉末、例えばＮｉ
合金粉末６を噴射し、同時にガス供給ノズル７よりシー
ルドガス８を噴射するものである。EXAMPLE FIG. 1 shows a local melt alloying process. In this treatment, a metal base material in which a fine spherical intermetallic compound is dispersed, for example, an Al alloy base material 1 is moved in the direction of the arrow, and its surface is irradiated with a laser beam 3 emitted from an oscillator 2. The powder is supplied to the molten pool 4 while being melted.
More carrier gas hardened alloy powder, eg Ni
The alloy powder 6 is sprayed, and at the same time, the shield gas 8 is sprayed from the gas supply nozzle 7.
【０００７】前記処理において、所定の条件を特定する
ことにより、図２に示す高強度構造部材９が得られる。
その部材９は部材本体１１と硬質表面層１０とを備え、
その部材本体１１と硬質表面層１０との間に、それら１
０，１１と一体に軟質中間層１２を有する。In the above process, the high-strength structural member 9 shown in FIG. 2 is obtained by specifying the predetermined conditions.
The member 9 comprises a member body 11 and a hard surface layer 10,
Between the member body 11 and the hard surface layer 10,
It has a soft intermediate layer 12 integrally with 0 and 11.
【０００８】硬質表面層１０は、前記処理において溶融
池４が冷却したものであり、母材１とＮｉ合金粉末６と
の合金化により形成される。The hard surface layer 10 is obtained by cooling the molten pool 4 in the above treatment, and is formed by alloying the base material 1 and the Ni alloy powder 6.
【０００９】また軟質中間層１２は、前記処理による熱
影響により母材１に含まれた微細で、且つ球状の金属間
化合物が粗大化すると共に針状化または／および塊状化
することによって形成される。The soft intermediate layer 12 is formed by coarsening and acicularization and / or agglomeration of the fine and spherical intermetallic compound contained in the base material 1 due to the heat effect of the above treatment. It
【００１０】このように、粗大化した針状または／およ
び塊状の金属間化合物がマトリックスに分散すると、そ
の金属間化合物がマトリックスの影響を受け易くなるた
め金属組織が軟化し、軟質中間層１２の硬度は硬質表面
層１０のそれよりも低いことは当然のこととして部材本
体１１の硬度よりも低くなり、これにより軟質中間層１
２は粘り強さを有する。As described above, when the coarse needle-shaped and / or lump-shaped intermetallic compound is dispersed in the matrix, the intermetallic compound is easily affected by the matrix, so that the metal structure is softened and the soft intermediate layer 12 has a soft structure. Needless to say, the hardness is lower than that of the hard surface layer 10, and thus lower than the hardness of the member main body 11, whereby the soft intermediate layer 1
2 has tenacity.
【００１１】前記のように構成すると、硬質表面層１０
に亀裂が発生しても、その亀裂の部材本体１１への伝播
を軟質中間層１２により抑制して構造部材９の高強度を
維持することが可能となる。When constituted as described above, the hard surface layer 10
Even if a crack is generated in the structural member 9, the propagation of the crack to the member body 11 can be suppressed by the soft intermediate layer 12, and the high strength of the structural member 9 can be maintained.
【００１２】この亀裂伝播抑制効果を得るためには、軟
質中間層１２の厚さｔは０．２mm≦ｔ≦０．８mmに設定
される。その理由は、軟質中間層１２の厚さｔが前記範
囲を逸脱すると、軟質中間層１２による亀裂伝播抑制効
果が減退するからである。In order to obtain this crack propagation suppressing effect, the thickness t of the soft intermediate layer 12 is set to 0.2 mm≤t≤0.8 mm. The reason is that if the thickness t of the soft intermediate layer 12 deviates from the above range, the effect of suppressing crack propagation by the soft intermediate layer 12 decreases.
【００１３】軟質中間層１２の厚さｔは、局部溶融合金
化処理の条件および母材１に含まれる金属間化合物の量
によって変化する。The thickness t of the soft intermediate layer 12 changes depending on the conditions of the local melt alloying treatment and the amount of the intermetallic compound contained in the base material 1.
【００１４】例えば、前記処理において、レーザビーム
３の出力、Ｎｉ合金粉末６の供給量および母材１に含ま
れる金属間化合物の量をそれぞれ一定とした場合、軟質
中間層１２の厚さｔは母材１の移動速度、したがって処
理速度に依存する。この場合、処理速度が遅くなるに従
って軟質中間層１２の厚さｔは増加する。For example, when the output of the laser beam 3, the supply amount of the Ni alloy powder 6 and the amount of the intermetallic compound contained in the base material 1 are constant in the above process, the thickness t of the soft intermediate layer 12 is It depends on the moving speed of the base material 1, and hence the processing speed. In this case, the thickness t of the soft intermediate layer 12 increases as the processing speed decreases.
【００１５】一方、前記処理においてレーザビーム３の
出力、Ｎｉ合金粉末６の供給量および処理速度をそれぞ
れ一定とした場合、軟質中間層１２の厚さｔは母材１に
含まれる金属間化合物の量によって影響を受ける。この
場合、母材１に含まれる金属間化合物の量、したがっ
て、その体積分率Ｖｆを１５％≦Ｖｆ≦６５％に設定す
ることにより、軟質中間層１２の厚さｔを前記範囲に収
めることができる。On the other hand, when the output of the laser beam 3, the supply amount of the Ni alloy powder 6 and the processing speed are constant in the above processing, the thickness t of the soft intermediate layer 12 depends on the intermetallic compound contained in the base material 1. Affected by quantity. In this case, the thickness t of the soft intermediate layer 12 is set within the above range by setting the amount of the intermetallic compound contained in the base material 1, that is, the volume fraction Vf thereof to 15% ≦ Vf ≦ 65%. You can
【００１６】以下、具体例について説明する。 I. 母材の製造 (i) Ａｌ−６重量％Ｃｒ−３重量％Ｆｅ−２重量％Ｚ
ｒといった組成を有する溶湯を調製し、その溶湯を用
い、湯温１２００℃、ノズルの直径２．８mmの条件下で
Ｎ2 ガスアトマイズ法を適用して急冷凝固Ａｌ合金粉末
を製造し、次いで、そのＡｌ合金粉末に分級処理を施し
て、粒径１０５μｍ以下の粉末を得た。A specific example will be described below. I. Manufacture of base material (i) Al-6 wt% Cr-3 wt% Fe-2 wt% Z
A melt having a composition such as r is prepared, and the melt is used to produce a rapidly solidified Al alloy powder by applying a N 2 gas atomizing method under the conditions of a melt temperature of 1200 ° C. and a nozzle diameter of 2.8 mm. The Al alloy powder was classified to obtain a powder having a particle size of 105 μm or less.
【００１７】(ii) 粒径１０５μｍ以下の前記Ａｌ合
金粉末を用い、加圧力４０００kg／cm 2 の条件下でＣＩ
Ｐ処理（冷間静水圧プレス処理）を行うことにより直径
７８mm、長さ６５mmの圧粉体を製造し、次いでその圧粉
体をＡｒガス流通下で４２０℃に加熱して脱ガス処理を
行った。(Ii) Al alloy having a grain size of 105 μm or less
Pressure of 4000kg / cm using gold powder 2CI under
Diameter by performing P treatment (cold isostatic press treatment)
78mm and 65mm length compacts are manufactured, and then the compacts
Degas by heating the body to 420 ° C under Ar gas flow
went.
【００１８】(iii) 脱ガス後の圧粉体を用い、加熱温
度４２０℃、押出し圧力４３０ton 、押出し速度２mm／
min の条件下で熱間押出し加工を行い、直径３２mmの押
出し材を製造し、その押出し材に機械加工を施して板状
母材１を得た。(Iii) Using the degassed green compact, heating temperature 420 ° C., extrusion pressure 430 tons, extrusion speed 2 mm /
Hot extrusion was performed under the condition of min to produce an extruded material having a diameter of 32 mm, and the extruded material was machined to obtain a plate-shaped base material 1.
【００１９】この母材１は、球状ＡｌＣｒＦｅ系金属間
化合物および球状ＡｌＺｒ系金属間化合物を含有し、そ
れら金属間化合物の体積分率ＶｆはＶｆ＝４０％であ
り、また平均粒径ｄはｄ＝０．５〜２．０μｍと微細で
あることが確認された。 II. 構造部材の製造 前記母材１に、図１に示す局部溶融合金化処理を施し
て、部材本体１１、軟質中間層１２および硬質表面層１
０を備えた構造部材９を製造した。This base material 1 contains a spherical AlCrFe-based intermetallic compound and a spherical AlZr-based intermetallic compound, the volume fraction Vf of these intermetallic compounds is Vf = 40%, and the average particle diameter d is d. = 0.5 to 2.0 μm, it was confirmed to be fine. II. Manufacture of Structural Member The base material 1 is subjected to the local melt alloying treatment shown in FIG. 1 to obtain a member main body 11, a soft intermediate layer 12 and a hard surface layer 1.
A structural member 9 with 0 was manufactured.
【００２０】処理条件は次の通りである。処理速度（母
材の移動速度）：１０００mm／min；レーザビーム：出
力３ｋＷ、ビーム直径３mm；キャリヤガス：Ｈｅガス、
供給量１１．５リットル／min ；硬質化合金粉末：Ｔａ
を２５重量％含有するＮｉ合金粉末、供給量６ｇ／min
；シールドガス：Ｈｅガス、供給量２０リットル／min
。硬質表面層１０の組成は、重量比で、母材成分：Ｎ
ｉ合金粉末＝１：２であった。The processing conditions are as follows. Processing speed (moving speed of base material): 1000 mm / min; laser beam: output 3 kW, beam diameter 3 mm; carrier gas: He gas,
Supply rate 11.5 liters / min; Hardened alloy powder: Ta
Alloy powder containing 25% by weight of iron, supply rate 6 g / min
; Shield gas: He gas, supply rate 20 liters / min
. The composition of the hard surface layer 10 is, by weight ratio, the base material component: N
The i alloy powder was 1: 2.
【００２１】図３は、構造部材９における硬度分布を示
す。本図より、硬質表面層１０の厚さは約１．３mm、軟
質中間層１２の厚さは約０．３mmであり、また軟質中間
層１２の硬度は硬質表面層１０および部材本体１１の硬
度よりも低いことが判る。この軟質中間層１２は、検鏡
の結果、マトリックス中に粗大化した針状および塊状金
属間化合物が略均一に分散した金属組織を有することが
確認された。FIG. 3 shows the hardness distribution in the structural member 9. From this figure, the thickness of the hard surface layer 10 is about 1.3 mm, the thickness of the soft intermediate layer 12 is about 0.3 mm, and the hardness of the soft intermediate layer 12 is the hardness of the hard surface layer 10 and the member body 11. It turns out that it is lower than. As a result of microscopic examination, it was confirmed that the soft intermediate layer 12 has a metal structure in which coarsened acicular and lumpy intermetallic compounds are substantially uniformly dispersed in the matrix.
【００２２】図４，図５は、軟質中間層の厚さを異にす
る各種構造部材の疲労試験結果を示す。疲労試験には両
振方式の板曲げ疲労試験機が用いられた。また試験は常
温下で行われ、繰返し速度は２５Ｈｚに設定された。4 and 5 show the results of fatigue tests of various structural members having different thicknesses of the soft intermediate layer. A double-vibration plate bending fatigue tester was used for the fatigue test. The test was performed at room temperature and the repetition rate was set to 25 Hz.
【００２３】図４において、各線ｘ1 〜ｘ4 で示す各種
構造部材と、処理速度および軟質中間層の厚さとの関係
は表１の通りである。母材としては前記のものと同一の
ものが用いられ、また他の処理条件は前記と同一に設定
された。In FIG. 4, the relationship between the various structural members indicated by the lines x 1 to x 4 , the processing speed and the thickness of the soft intermediate layer is as shown in Table 1. The same base material as described above was used, and the other processing conditions were set to the same as above.
【００２４】[0024]
【表１】 図４、線ｘ4 の構造部材は、表１から明らかなように図
３の構造部材に該当する。[Table 1] The structural member of FIG. 4, line x 4 corresponds to the structural member of FIG. 3, as is apparent from Table 1.
【００２５】図４、表１より軟質中間層の厚さの増加に
伴い、構造部材の疲労強度が向上することが判る。It can be seen from FIG. 4 and Table 1 that the fatigue strength of the structural member is improved as the thickness of the soft intermediate layer is increased.
【００２６】図５において、各点ｙ1 〜ｙ5 で示す各種
構造部材と、処理速度および軟質中間層の厚さとの関係
は表２の通りである。母材としては前記のものと同一の
ものが用いられ、また他の処理条件は前記と同一に設定
された。図５の疲労限は繰返し回数１０7 回における値
である。In FIG. 5, the relationship between various structural members indicated by points y 1 to y 5 , the processing speed and the thickness of the soft intermediate layer is as shown in Table 2. The same base material as described above was used, and the other processing conditions were set to the same as above. The fatigue limit in FIG. 5 is a value when the number of repetitions is 10 7 .
【００２７】[0027]
【表２】 図５、点ｙ3 の構造部材は、表２から明らかなように図
３の構造部材に該当する。[Table 2] The structural member at point y 3 in FIG. 5 corresponds to the structural member in FIG. 3 as is apparent from Table 2.
【００２８】図５、表２から明らかなように軟質中間層
の厚さｔが０．１mm≦ｔ≦０．３mmであるときには、そ
の厚さｔの増加に伴い構造部材の疲労強度は急激に向上
するが、軟質中間層の厚さｔが０．３＜ｔ≦０．８mmに
なると構造部材の疲労強度は緩やかに低下し、さらに軟
質中間層の厚さｔがｔ＞０．８mmになると構造部材の疲
労強度は急激に低下する。As is clear from FIG. 5 and Table 2, when the thickness t of the soft intermediate layer is 0.1 mm ≦ t ≦ 0.3 mm, the fatigue strength of the structural member rapidly increases as the thickness t increases. Although improved, when the thickness t of the soft intermediate layer becomes 0.3 <t ≦ 0.8 mm, the fatigue strength of the structural member gradually decreases, and when the thickness t of the soft intermediate layer becomes t> 0.8 mm. The fatigue strength of structural members drops sharply.
【００２９】図４，図５から明らかなように、軟質中間
層の亀裂伝播抑制効果を得て構造部材の高強度を維持す
るためには、軟質中間層の厚さｔを０．２mm≦ｔ≦０．
８mmに設定することが必要であり、好ましくはｔ＝０．
３mmである。As is clear from FIGS. 4 and 5, in order to obtain the crack propagation suppressing effect of the soft intermediate layer and maintain the high strength of the structural member, the thickness t of the soft intermediate layer is 0.2 mm ≦ t. ≤0.
It is necessary to set it to 8 mm, preferably t = 0.
It is 3 mm.
【００３０】図６は、母材における金属間化合物の体積
分率Ｖｆと構造部材における軟質中間層の厚さとの関係
を示す。FIG. 6 shows the relationship between the volume fraction Vf of the intermetallic compound in the base material and the thickness of the soft intermediate layer in the structural member.
【００３１】金属間化合物の体積分率Ｖｆの変化は、母
材の組成を変えることによって行われ、各構造部材を得
るための処理条件は図３の構造部材のそれと同一に設定
された。The change in the volume fraction Vf of the intermetallic compound was performed by changing the composition of the base material, and the processing conditions for obtaining each structural member were set to be the same as those of the structural member of FIG.
【００３２】図６において、各点ｚ1 〜ｚ7 で示す各種
構造部材と、母材の組成およびその金属間化合物の体積
分率Ｖｆとの関係は表３の通りである。Table 3 shows the relationship between various structural members indicated by points z 1 to z 7 in FIG. 6, the composition of the base material, and the volume fraction Vf of the intermetallic compound.
【００３３】[0033]
【表３】 図６、点ｚ3 の構造部材は、表３から明らかなように図
３の構造部材に該当する。[Table 3] The structural member at point z 3 in FIG. 6 corresponds to the structural member in FIG. 3 as is apparent from Table 3.
【００３４】図６から明らかなように、母材における金
属間化合物の体積分率Ｖｆを１５％≦Ｖｆ≦６５％に設
定することによって、軟質中間層の厚さｔを０．２mm≦
ｔ≦０．８mmの範囲に収めることができる。As is apparent from FIG. 6, by setting the volume fraction Vf of the intermetallic compound in the base material to be 15% ≦ Vf ≦ 65%, the thickness t of the soft intermediate layer is 0.2 mm ≦.
It can be set within the range of t ≦ 0.8 mm.
【００３５】[0035]
【発明の効果】本発明によれば、部材本体と局部溶融合
金化処理による硬質表面層との間に、前記のような軟質
中間層を介在させることにより、その軟質中間層による
亀裂伝播抑制効果を得て、高強度を維持された構造部材
を提供することができる。According to the present invention, by interposing the soft intermediate layer as described above between the member main body and the hard surface layer formed by the local melt alloying treatment, the effect of suppressing crack propagation by the soft intermediate layer. Therefore, it is possible to provide a structural member in which high strength is maintained.
【図１】局部溶融合金化処理の説明図である。FIG. 1 is an explanatory diagram of a local molten alloying process.
【図２】構造部材の断面図である。FIG. 2 is a sectional view of a structural member.
【図３】構造部材において、表面からの距離と硬さとの
関係を示すグラフである。FIG. 3 is a graph showing the relationship between the distance from the surface and hardness in the structural member.
【図４】疲労試験において、繰返し回数と荷重振幅との
関係を示すグラフである。FIG. 4 is a graph showing the relationship between the number of repetitions and the load amplitude in a fatigue test.
【図５】疲労試験において、軟質中間層の厚さと疲労限
との関係を示すグラフである。FIG. 5 is a graph showing the relationship between the thickness of the soft intermediate layer and the fatigue limit in a fatigue test.
【図６】母材における金属間化合物の体積分率と構造部
材における軟質中間層の厚さとの関係を示すグラフであ
る。FIG. 6 is a graph showing the relationship between the volume fraction of the intermetallic compound in the base material and the thickness of the soft intermediate layer in the structural member.
１ 母材 ９ 構造部材 １０ 硬質表面層 １１ 部材本体 １２ 軟質中間層 1 Base Material 9 Structural Member 10 Hard Surface Layer 11 Member Main Body 12 Soft Intermediate Layer
───────────────────────────────────────────────────── フロントページの続き (72)発明者 馬場 剛志 埼玉県和光市中央１丁目４番１号 株式会 社本田技術研究所内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Takeshi Baba 1-4-1 Chuo, Wako City, Saitama Prefecture Honda R & D Co., Ltd.
Claims (4)
金化処理により形成される硬質表面層（１０）を設けた
高強度構造部材において、前記部材本体（１１）と硬質
表面層（１０）との間に、それら（１０，１１）と一体
で、且つ前記硬質表面層（１０）よりも低硬度の軟質中
間層（１２）を介在させたことを特徴とする高強度構造
部材。1. A high-strength structural member comprising a metal member body (11) provided with a hard surface layer (10) formed by local melt alloying treatment, wherein the member body (11) and the hard surface layer (10). ), A soft intermediate layer (12) which is integral with these (10, 11) and has a lower hardness than the hard surface layer (10) is interposed.
２mm≦ｔ≦０．８mmである、請求項１記載の高強度構造
部材。2. The thickness t of the soft intermediate layer (12) is 0.
The high-strength structural member according to claim 1, wherein 2 mm ≦ t ≦ 0.8 mm.
合物の体積分率Ｖｆは１５％≦Ｖｆ≦６５％である、請
求項１または２記載の高強度構造部材。3. The high strength structural member according to claim 1, wherein the volume fraction Vf of the intermetallic compound in the metal base material (1) is 15% ≦ Vf ≦ 65%.
化合物は針状および塊状の少なくとも一方の形状を有す
る、請求項１，２または３記載の高強度構造部材。4. The high-strength structural member according to claim 1, wherein the intermetallic compound in the soft intermediate layer (12) has at least one of a needle shape and a lump shape.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP326192A JPH05186882A (en) | 1992-01-10 | 1992-01-10 | High strength structural member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP326192A JPH05186882A (en) | 1992-01-10 | 1992-01-10 | High strength structural member |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05186882A true JPH05186882A (en) | 1993-07-27 |
Family
ID=11552531
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP326192A Pending JPH05186882A (en) | 1992-01-10 | 1992-01-10 | High strength structural member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05186882A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4943558B2 (en) * | 2009-08-31 | 2012-05-30 | 新日本製鐵株式会社 | High-strength hot-dip galvanized steel sheet and manufacturing method thereof |
-
1992
- 1992-01-10 JP JP326192A patent/JPH05186882A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4943558B2 (en) * | 2009-08-31 | 2012-05-30 | 新日本製鐵株式会社 | High-strength hot-dip galvanized steel sheet and manufacturing method thereof |
| US9109275B2 (en) | 2009-08-31 | 2015-08-18 | Nippon Steel & Sumitomo Metal Corporation | High-strength galvanized steel sheet and method of manufacturing the same |
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