JP2003034855A - High-strength aluminum plated steel sheet superior in corrosion resistance after coating, and member for automobile using the same - Google Patents
High-strength aluminum plated steel sheet superior in corrosion resistance after coating, and member for automobile using the sameInfo
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- JP2003034855A JP2003034855A JP2001220807A JP2001220807A JP2003034855A JP 2003034855 A JP2003034855 A JP 2003034855A JP 2001220807 A JP2001220807 A JP 2001220807A JP 2001220807 A JP2001220807 A JP 2001220807A JP 2003034855 A JP2003034855 A JP 2003034855A
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- corrosion resistance
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、自動車の足回り等
の高強度を要求される部材、及びこれを製造するための
鋼素材に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a member that is required to have high strength, such as an underbody of an automobile, and a steel material for manufacturing the member.
【０００２】[0002]
【従来の技術】近年、地球環境問題を発端とした低燃費
化の動きから自動車用鋼板に対しては高強度化に対する
要望が強い。しかし、一般に高強度化は加工性、成形性
の低下を伴い、高強度、高成形性を両立する鋼板が要望
されている。これに対する一つの回答は、残留オーステ
ナイトのマルテンサイト変態を利用したＴＲＩＰ（ＴＲ
ａｎｓｆｏｒｍａｔｉｏｎ Ｉｎｄｕｃｅｄ Ｐｌａｃ
ｉｔｉｃｉｔｙ）鋼であり、近年用途が拡大しつつあ
る。しかし、この鋼により、成形性の優れた１０００Ｍ
Ｐａ級の高強度鋼板を製造することが可能であるが、更
に、高強度、例えば１５００ＭＰａ以上というような超
高強度鋼で成形性を確保することは困難である。2. Description of the Related Art In recent years, there has been a strong demand for high strength steel sheets for automobiles due to the movement toward lower fuel consumption caused by global environmental problems. However, in general, higher strength is accompanied by lowering of workability and formability, and a steel sheet satisfying both high strength and high formability is desired. One answer to this is TRIP (TRIP) that utilizes the martensitic transformation of retained austenite.
transformation Induced Plac
steel), and its applications are expanding in recent years. However, due to this steel, it has excellent formability of 1000M.
Although it is possible to manufacture a high-strength steel sheet of the Pa class, it is difficult to secure formability with high-strength steel, for example, ultra-high-strength steel having a strength of 1500 MPa or more.
【０００３】そこで、高強度、高成形性を両立する別の
形として最近注目を浴びているのがホットプレスであ
る。これは鋼板を８００℃以上の高温に加熱した状態で
成形することにより高強度鋼板の成形性の課題を無く
し、成型後の冷却により焼きを入れて所望の材質を得る
というものである。しかし、大気中での加熱を伴うた
め、表面に酸化物が生成してこれを後工程で除去する必
要がある。これを改善したものが特開２０００−３８６
４０号公報であり、０．１５〜０．５％の炭素を含有す
る鋼板にアルミめっきして加熱時の酸化抑制を図ってい
る。もう一つの形として、鋼板を常温で成型後、一部分
を急速加熱し、急冷して焼きを入れて高強度を得るとい
う手法も有り得る。この場合、局部的に加熱すること
で、高強度が必要とされる部位のみの強度を高めること
が可能である。Therefore, hot pressing has recently been attracting attention as another form that achieves both high strength and high formability. This is to eliminate the problem of formability of a high-strength steel sheet by forming the steel sheet in a state where it is heated to a high temperature of 800 ° C. or higher, and quench it by cooling after forming to obtain a desired material. However, since it is accompanied by heating in the atmosphere, an oxide is generated on the surface and needs to be removed in a later step. What improved this is Unexamined-Japanese-Patent No. 2000-386.
No. 40 publication, a steel plate containing 0.15 to 0.5% of carbon is aluminized to suppress oxidation during heating. As another form, there may be a method in which a steel sheet is formed at room temperature, and then a portion of the steel sheet is rapidly heated and then rapidly cooled to obtain high strength. In this case, by locally heating, it is possible to increase the strength of only the portion where high strength is required.
【０００４】[0004]
【発明が解決しようとする課題】これらの発明は高強度
の成形部品を効率良く製造するのに有効であるが、通常
プレスされた後、塗装されて使用に供されるが、アルミ
めっき層はクラックを生じやすいという欠点を有してお
り、厳しい成形をした後には、これらクラックを起点と
して腐食が開始され、塗装後耐食性が低下するという問
題があった。These inventions are effective for efficiently producing a high-strength molded part, but they are usually pressed and then painted for use, but the aluminum plating layer is not used. It has a drawback that cracks are likely to occur, and after severe molding, corrosion starts from these cracks, and there is a problem that the corrosion resistance after coating is lowered.
【０００５】[0005]
【課題を解決するための手段】本発明者らは、上記のよ
うな課題を克服するためにアルミめっき鋼板の加工後の
耐食性への影響因子を詳細に検討した結果、次の知見を
得た。すなわち、ホットプレス、局部的な急速加熱を行
った後のアルミめっき層は表面まで金属間化合物に変化
しており、この化合物は非常に脆性であり、加工時にク
ラックを生じやすい。また、この相は母材鋼板よりも貴
な電位を有するため、クラックを起点として鋼素地の腐
食が開始され、塗装後耐食性の低下を招きやすい。この
塗装後耐食性低下を回避するには、この金属間化合物中
にＭｎを添加することが非常に有効である。Ｍｎの果た
す作用は未だ未解明ながらも、Ｍｎは合金層の電位を制
御してＦｅ−Ａｌ系の金属間化合物相電位を鋼板のそれ
に近づける作用を持つと言われており、その作用に加え
て塗装前処理の化成処理時のリン酸塩結晶形態も制御し
ている可能性もある。このとき母材鋼板は焼入れ後の強
度を確保するためにある程度以上のＣが必要である。Means for Solving the Problems The present inventors have obtained the following findings as a result of detailed investigation of factors affecting corrosion resistance of aluminum plated steel sheets after processing in order to overcome the above problems. . That is, the aluminum plating layer after hot pressing and local rapid heating is transformed into an intermetallic compound up to the surface, and this compound is extremely brittle and easily cracks during processing. Further, since this phase has a nobler potential than that of the base steel sheet, corrosion of the steel base is started from a crack as a starting point and the corrosion resistance after coating is likely to be deteriorated. In order to avoid the deterioration of the corrosion resistance after coating, it is very effective to add Mn to the intermetallic compound. Although the action of Mn has not been clarified yet, it is said that Mn has the action of controlling the potential of the alloy layer to bring the Fe-Al-based intermetallic compound phase potential closer to that of the steel sheet. It is possible that the phosphate crystal morphology during the chemical conversion treatment before coating is also controlled. At this time, the base material steel plate needs a certain amount of C or more to secure the strength after quenching.
【０００６】[0006]
【発明の実施の形態】次に、本発明の限定理由について
説明する。
Ｃ：０．０５〜０．７％
Ｃ：は、成型後に１０００ＭＰａ以上の高強度を有する
ものであり、ホットプレスあるいは局部急速加熱後に急
冷してマルテンサイトを主体とする組織に変態させるも
のであり、そのためにはＣ量０．０５％が必要である。
一方、Ｃ量を０．７％を超えても強度が飽和してしまう
ことに加え、溶接割れを生じやすくするため、その上限
を０．７％に定める。BEST MODE FOR CARRYING OUT THE INVENTION Next, the reasons for limitation of the present invention will be described. C: 0.05 to 0.7% C: has a high strength of 1000 MPa or more after molding, and is rapidly cooled after hot pressing or local rapid heating to transform into a structure mainly composed of martensite. Therefore, a C content of 0.05% is necessary.
On the other hand, even if the C content exceeds 0.7%, the strength is saturated and the upper limit is set to 0.7% in order to easily cause weld cracking.
【０００７】他の鋼中元素については、特に規定を設け
ないが、Ｓｉ，Ｍｎ，Ｔｉ，Ｂ，Ｃｒ，Ｍｏ，Ａｌ，
Ｐ，Ｓ，Ｎ等の元素が通常使われ得る。Ｓｉは、疲労特
性に効果があり、Ｍｎ，Ｂは、焼入れ性の向上に寄与す
る。Ｔｉ，Ｓｉ，Ｃｒ，Ｍｏ，Ａｌは、またアルミめっ
き後の耐熱性を向上させる元素である。本発明における
Ｍｎは鋼中に添加することも、めっき浴に添加すること
も可能である。どちらの手法でも加熱後に０．１％以上
金属間化合物相に含有させることによって、良好な塗装
後耐食性が得られる。なお、生成する金属間化合物とし
ては、ＦｅＡｌ3 ，Ｆｅ2 Ａｌ5 ，Ｆｅ3 Ａｌ，Ｆｅ2
Ａｌ8 Ｓｉ等が生成し得る。Ｍｎは、Ｆｅに近い原子半
径を有しているため、Ｆｅと置換した形として存在する
と思われる。Other elements in the steel are not specified, but Si, Mn, Ti, B, Cr, Mo, Al,
Elements such as P, S, N can usually be used. Si has an effect on fatigue characteristics, and Mn and B contribute to improvement of hardenability. Ti, Si, Cr, Mo and Al are also elements that improve the heat resistance after aluminum plating. Mn in the present invention can be added to the steel or the plating bath. In either method, good post-coating corrosion resistance can be obtained by including 0.1% or more in the intermetallic compound phase after heating. In addition, as the intermetallic compound generated, FeAl 3 , Fe 2 Al 5 , Fe 3 Al, Fe 2
Al 8 Si or the like can be generated. Since Mn has an atomic radius close to that of Fe, it is considered that Mn exists as a form substituted with Fe.
【０００８】アルミめっき鋼板は、通常Ｆｅ−Ａｌ系合
金層が成長して加工性を低下させやすく、この合金層の
成長を抑制して加工性を向上させるためにＳｉが添加さ
れることが多い。ホットプレスの場合には加熱して表面
まで合金化させた後に、熱間で加工するためにＳｉは特
に添加する必要はない。しかし、当然添加することも可
能である。局部急速加熱の場合には、常温で加工するた
め、Ｓｉは必須である。Ｓｉは、Ｆｅ−Ａｌの相互拡散
を抑制する効果があるため、鋼にＭｎを添加している場
合には鋼からのＭｎの拡散は抑制される傾向にある。[0008] In an aluminized steel sheet, a Fe-Al alloy layer usually grows and the workability is easily deteriorated, and Si is often added to suppress the growth of the alloy layer and improve the workability. . In the case of hot pressing, it is not necessary to add Si for hot working after heating to alloy the surface. However, it is of course possible to add it. In the case of local rapid heating, Si is essential because it is processed at room temperature. Since Si has the effect of suppressing the mutual diffusion of Fe-Al, when Mn is added to the steel, the diffusion of Mn from the steel tends to be suppressed.
【０００９】一方、めっき浴にＭｎを添加している場合
には逆にＭｎ濃度が高目に出る傾向にある。アルミめっ
きの添加元素として、他にＣｒ，Ｍｇ，Ｔｉ，Ｓｂ，Ｓ
ｎ，Ｚｎ等が考えられるが、めっき層がＡｌを主体とす
る限り、適用可能である。しかし、Ｚｎは沸点が低く、
大量に添加すると加熱時に表面に粉体状のＺｎを生成し
て、プレス時のカジリを惹起するため、６０％以上の添
加は望ましくない。On the other hand, when Mn is added to the plating bath, on the contrary, the Mn concentration tends to be high. In addition to Cr, Mg, Ti, Sb, S as additional elements of aluminum plating
Although n, Zn, etc. are conceivable, they are applicable as long as the plating layer is mainly composed of Al. However, Zn has a low boiling point,
If added in a large amount, powdery Zn is generated on the surface during heating, causing galling during pressing, so addition of 60% or more is not desirable.
【００１０】本発明において、アルミめっきの付着量、
めっき前処理、後処理、プレス時の鋼板の加熱方法、冷
却方法等については特に限定するものではない。めっき
付着量は通常の片面３０〜１００ｇ／ｍ2 の範囲ではな
んら問題ない。めっき後処理として一次防錆、潤滑性を
目的としてクロメート処理、樹脂被覆処理等ありうる
が、有機樹脂は加熱すると消失してしまうため好ましく
ない。クロメート処理も近年の６価クロム規制を考慮す
ると、電解クロメート等の３価の処理皮膜が好ましい。In the present invention, the adhesion amount of aluminum plating,
The pretreatment, posttreatment, heating method and cooling method of the steel sheet during pressing are not particularly limited. There is no problem if the coating weight is in the range of 30-100 g / m 2 on one side. Although post-plating treatment may include primary rust prevention, chromate treatment for the purpose of lubricity, resin coating treatment, etc., it is not preferable because the organic resin disappears when heated. Considering the recent regulation of hexavalent chromium, the chromate treatment is preferably a trivalent treatment film such as electrolytic chromate.
【００１１】アルミめっき鋼板の製造法についても何ら
限定するものではない。通常の製鋼、熱延条件が適用可
能である。アルミめっきは通常溶融めっき法で施される
が、これに限定せず、非水溶媒からの電気めっき、蒸着
処理等も使用可能である。めっき前処理としてＮｉプレ
めっき等もありうるが、これも適用可能である。加熱，
冷却の方法についても特に限定しない。通電加熱、炉内
加熱、誘導加熱、高周波加熱等の加熱手段がありうる。
中でも局部的な急速加熱には、高周波加熱が適してい
る。There is no limitation on the method of manufacturing the aluminized steel sheet. Normal steelmaking and hot rolling conditions can be applied. The aluminum plating is usually performed by a hot dipping method, but not limited to this, and electroplating from a nonaqueous solvent, vapor deposition treatment, etc. can also be used. As the pretreatment for plating, Ni pre-plating or the like may be used, but this is also applicable. heating,
The cooling method is also not particularly limited. There may be heating means such as electric heating, furnace heating, induction heating, and high frequency heating.
Among them, high frequency heating is suitable for local rapid heating.
【００１２】金属間化合物中のＭｎ量の測定法は特に規
定するものではないが、例えば断面研磨してＥＰＭＡ等
でスポット定量分析することで金属間化合物の組成を測
定することができる。Ｍｎに加えて、当然ＡｌとＦｅが
主成分であり、通常この２つの元素で９５％程度を占め
る。その他、鋼中、めっき浴中の添加元素を含有してい
る。The method for measuring the amount of Mn in the intermetallic compound is not particularly specified, but the composition of the intermetallic compound can be measured by, for example, polishing the cross section and performing spot quantitative analysis with EPMA or the like. In addition to Mn, naturally Al and Fe are the main components, and these two elements usually account for about 95%. In addition, it contains additional elements in steel and plating bath.
【００１３】[0013]
【実施例】次に、実施例で本発明をより詳細に説明す
る。
（実施例１）通常の熱延、冷延工程を経た、表１に示す
ような鋼成分の酸洗鋼板（板厚１．８ｍｍ）、冷延鋼板
（板厚１．２ｍｍ）を材料として、溶融アルミめっきを
行った。表１のＮｏ．１、３、５、７は冷延鋼板であ
り、残りは熱延鋼板である。溶融アルミめっきは無酸化
炉−還元炉タイプのラインを使用し、めっき後ガスワイ
ピング法でめっき付着量を片面４０ｇ／ｍ2 に調節し、
その後冷却し、ゼロスパングル処理を施した。この際の
めっき浴組成としてはＡｌ−１０％Ｓｉ−２％Ｆｅであ
った。浴中のＦｅは浴中のめっき機器やストリップから
供給される不可避のものである。めっき外観は不めっき
等なく良好であった。このようにして製造した溶融アル
ミめっき鋼板の焼入れ性、表面金属間化合物中のＭｎ
量、硬度、塗装後耐食性を評価した。EXAMPLES Next, the present invention will be described in more detail by way of examples. (Example 1) As a material, a pickled steel sheet (sheet thickness 1.8 mm) and a cold rolled steel sheet (sheet thickness 1.2 mm) having steel components as shown in Table 1 which have undergone ordinary hot rolling and cold rolling steps are used. Hot-dip aluminum plating was performed. No. of Table 1 1, 3, 5, and 7 are cold rolled steel sheets, and the rest are hot rolled steel sheets. For hot dip aluminum plating, a non-oxidizing furnace-reducing furnace type line is used, and after plating, the coating amount is adjusted to 40 g / m 2 on one side by the gas wiping method.
After that, it was cooled and subjected to zero spangle treatment. The composition of the plating bath at this time was Al-10% Si-2% Fe. Fe in the bath is unavoidable supplied from plating equipment and strips in the bath. The plating appearance was good with no plating. Hardenability of the hot-dip aluminized steel sheet thus produced, Mn in the surface intermetallic compound
The amount, hardness and corrosion resistance after coating were evaluated.
【００１４】まず、焼入れ性については、鋼板を大気中
で９５０℃に５分加熱した後、平板のまま金型で押付け
て冷却した。こうして表面まで合金化させた、ほぼ均一
な外観の焼入れ板が得られた。このときの冷却速度は約
３００℃／秒であった。Ｍｎ量は断面研磨後、ＥＰＭＡ
定量分析を深さ方向に５点行い、その平均値とした。硬
度については、鋼板断面の中心部のビッカース硬度を荷
重１００ｇで測定した。Ａｌ，Ｆｅ，Ｚｎめっき共用の
化成処理液で約２分の化成処理を行った後、カチオン系
電着塗装を２０μｍ塗装し、１４０℃で２０分焼付け
た。その後、クロスカットを入れて塩水噴霧試験に供し
た。２０日後のクロスカットからの素地の腐食深さで塗
装後耐食性を判定した。なお、クロスカット時のカッタ
ーの切込み深さが約５０μｍであった。評価結果を表２
にまとめる。First, regarding the hardenability, the steel sheet was heated to 950 ° C. for 5 minutes in the atmosphere, and then pressed as it was with a mold to cool it. Thus, a quenched plate having a substantially uniform appearance, which was alloyed to the surface, was obtained. The cooling rate at this time was about 300 ° C./sec. After the cross-section polishing, Mn content is
Quantitative analysis was performed at 5 points in the depth direction, and the average value was obtained. Regarding hardness, the Vickers hardness of the central portion of the steel plate cross section was measured under a load of 100 g. After performing a chemical conversion treatment for about 2 minutes with a chemical conversion treatment solution common to Al, Fe, and Zn plating, a cationic electrodeposition coating was applied to 20 μm and baked at 140 ° C. for 20 minutes. After that, a cross cut was put in and subjected to a salt spray test. Corrosion resistance after coating was judged by the corrosion depth of the substrate from the cross cut after 20 days. The cutting depth of the cutter at the time of cross cutting was about 50 μm. Table 2 shows the evaluation results
Put together.
【００１５】[0015]
【表１】 [Table 1]
【００１６】[0016]
【表２】 [Table 2]
【００１７】〔塗装後耐食性の評価基準〕
○：腐食深さ８０μｍ以下
×：腐食深さ８０μｍ超
表２のＮｏ．８のようにＣが低すぎると十分な強度が得
られない。ビッカース硬度は一般に３倍するとその材料
の強度（ＭＰａ）に近い値となるが、この場合、７００
ＭＰａクラスの強度しか得られない。一方、Ｎｏ．７の
ように鋼中Ｍｎ、金属間化合物中のＭｎが低い系では塗
装後耐食性に劣る結果となった。鋼中元素の添加量が適
正に制御された、Ｎｏ．１〜６については、強度，耐熱
性の双方とも良好な結果が得られた。[Evaluation Criteria for Corrosion Resistance After Coating] ◯: Corrosion depth of 80 μm or less ×: Corrosion depth of more than 80 μm If C is too low as in No. 8, sufficient strength cannot be obtained. Generally, the Vickers hardness becomes a value close to the strength (MPa) of the material when tripled, but in this case, 700
Only strength in the MPa class can be obtained. On the other hand, No. As shown in No. 7, in a system in which Mn in steel and Mn in intermetallic compounds are low, the corrosion resistance after coating was poor. No. 3, in which the addition amount of the element in the steel was properly controlled. Regarding 1 to 6, good results were obtained in both strength and heat resistance.
【００１８】（実施例２）実施例１の表１中のＮｏ．７
の鋼を使用して、Ａｌ−１０％Ｓｉ−２％Ｆｅをベース
としてめっき浴中にＭｎを添加しためっきを行った。め
っき付着量は片面４０ｇ／ｍ2 であり、良好なめっき外
観が得られた。このときの浴中Ｍｎ量と、実施例１と同
じ条件で焼入れを行った後に実施例１と同じ評価項目で
評価した結果を表３にまとめる。Ｎｏ．１のように、金
属間化合物中のＭｎ量が少ないと、塗装後耐食性は不良
であるが、浴中にＭｎを添加するに従って、耐食性は向
上する。このときの金属間化合物中のＭｎ量と塗装後耐
食性の関係を図１に示す。Ｍｎ量により、塗装後耐食性
が向上していくことが見てとれる。(Example 2) No. 1 in Table 1 of Example 1 7
The steel of No. 1 was used to perform plating with Mn added in the plating bath based on Al-10% Si-2% Fe. The coating weight was 40 g / m 2 on one side, and a good plating appearance was obtained. Table 3 summarizes the amount of Mn in the bath at this time and the results of evaluation with the same evaluation items as in Example 1 after quenching under the same conditions as in Example 1. No. When the amount of Mn in the intermetallic compound is small as in No. 1, the corrosion resistance after coating is poor, but the corrosion resistance improves as Mn is added to the bath. The relationship between the amount of Mn in the intermetallic compound and the corrosion resistance after coating at this time is shown in FIG. It can be seen that the corrosion resistance after coating is improved depending on the amount of Mn.
【００１９】[0019]
【表３】 [Table 3]
【００２０】[0020]
【発明の効果】以上述べたように、本発明は塗装後の耐
食性に優れた高強度自動車部品とそれを構成する材料で
あるアルミめっき鋼板を提供する。本発明は、今後の自
動車軽量化に大きく寄与するものと思われ、産業上の寄
与は大きい。INDUSTRIAL APPLICABILITY As described above, the present invention provides a high-strength automobile part having excellent corrosion resistance after painting and an aluminum-plated steel plate which is a material constituting the same. The present invention is expected to make a great contribution to the weight reduction of automobiles in the future, and makes a great contribution to industry.
【図１】金属間化合物中のＭｎ量と塗装後の耐食性への
影響を示す図である。FIG. 1 is a diagram showing the effect on the amount of Mn in an intermetallic compound and the corrosion resistance after coating.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 末廣 正芳 福岡県北九州市戸畑区飛幡町１番１号 新 日本製鐵株式会社八幡製鐵所内 (72)発明者 宮腰 寿拓 福岡県北九州市戸畑区飛幡町１番１号 新 日本製鐵株式会社八幡製鐵所内 Ｆターム(参考） 4K027 AA02 AA05 AA23 AB02 AB06 AB09 AB32 AB48 AE03 AE11 AE21 AE27 ─────────────────────────────────────────────────── ─── Continued front page (72) Inventor Masayoshi Suehiro No. 1-1 Tobatacho, Tobata-ku, Kitakyushu City, Fukuoka Prefecture New Nippon Steel Co., Ltd., Yawata Works (72) Inventor, Hisashi Miyakoshi No. 1-1 Tobatacho, Tobata-ku, Kitakyushu City, Fukuoka Prefecture New Nippon Steel Co., Ltd., Yawata Works F-term (reference) 4K027 AA02 AA05 AA23 AB02 AB06 AB09 AB32 AB48 AE03 AE11 AE21 AE27
Claims (3)
有する鋼の表面に、Ａｌ，Ｆｅを主成分とし、Ｍｎを
０．１％以上含有する金属間化合物を有することを特徴
とする塗装後耐食性に優れた高強度アルミめっき鋼板。1. An intermetallic compound containing Al and Fe as main components and 0.1% or more of Mn on the surface of steel containing C: 0.05 to 0.7% by mass. A high-strength aluminum-plated steel sheet with excellent corrosion resistance after painting.
２０％含有することを特徴とする塗装後耐食性に優れた
高強度アルミめっき鋼板。2. A part of the intermetallic compound further contains 1 to Si.
A high-strength aluminum-plated steel sheet having excellent corrosion resistance after painting, which is characterized by containing 20%.
鋼板を使用することを特徴とする塗装後耐食性に優れた
自動車用部材。3. An automotive member having excellent corrosion resistance after painting, characterized by using the aluminum-plated steel sheet according to claim 1.
Priority Applications (9)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001220807A JP4612240B2 (en) | 2001-07-23 | 2001-07-23 | High-strength aluminized steel sheet with excellent corrosion resistance after painting and automotive parts using it |
| TW091113018A TWI317383B (en) | 2001-06-15 | 2002-06-14 | High-strength alloyed aluminum-system plated steel sheet and high-strength automotive part excellent in heat resistance and after-painting corrosion resistance |
| KR1020087029007A KR20080108163A (en) | 2001-06-15 | 2002-06-14 | Hot press method of high-strength alloyed aluminum-system palted steel sheet |
| AU2002309283A AU2002309283B2 (en) | 2001-06-15 | 2002-06-14 | High-strength Alloyed Aluminum-system Plated Steel Sheet and High-strength Automotive Part Excellent in Heat Resistance and After-painting Corrosion Resistance |
| PCT/JP2002/005978 WO2002103073A2 (en) | 2001-06-15 | 2002-06-14 | High-strength alloyed aluminum-system plated steel sheet and high-strength automotive part excellent in heat resistance and after-painting corrosion resistance |
| KR1020037016351A KR100836282B1 (en) | 2001-06-15 | 2002-06-14 | High-strength alloyed aluminum-system palted steel sheet |
| KR1020077027723A KR20070119096A (en) | 2001-06-15 | 2002-06-14 | High-strength alloyed aluminum-system palted steel sheet |
| CNB028120361A CN100370054C (en) | 2001-06-15 | 2002-06-14 | High-strength alloyed aluminum-system plated steel sheet and high-strength automotive part excellent in heat resistance and after-painting corrosion resistance |
| KR1020077017549A KR20070087240A (en) | 2001-06-15 | 2002-06-14 | Hot press method of high-strength alloyed aluminum-system palted steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001220807A JP4612240B2 (en) | 2001-07-23 | 2001-07-23 | High-strength aluminized steel sheet with excellent corrosion resistance after painting and automotive parts using it |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2003034855A true JP2003034855A (en) | 2003-02-07 |
| JP4612240B2 JP4612240B2 (en) | 2011-01-12 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2001220807A Expired - Fee Related JP4612240B2 (en) | 2001-06-15 | 2001-07-23 | High-strength aluminized steel sheet with excellent corrosion resistance after painting and automotive parts using it |
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006152427A (en) * | 2004-10-29 | 2006-06-15 | Sumitomo Metal Ind Ltd | Hot-pressed steel sheet member, manufacturing method therefor and steel sheet to be hot-pressed |
| JP2008195999A (en) * | 2007-02-13 | 2008-08-28 | Jfe Steel Kk | Steel sheet for hot press, and method for producing the same |
| JP2008223084A (en) * | 2007-03-13 | 2008-09-25 | Nippon Steel Corp | Al PLATED STEEL SHEET FOR HOT PRESSING |
| JP2008285757A (en) * | 2008-05-27 | 2008-11-27 | Nippon Steel Corp | High-strength automobile component having excellent corrosion resistance after coating |
| WO2012137687A1 (en) | 2011-04-01 | 2012-10-11 | 新日本製鐵株式会社 | Hot stamp-molded high-strength component having excellent corrosion resistance after coating, and method for manufacturing same |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09156027A (en) * | 1995-12-08 | 1997-06-17 | Nippon Steel Corp | Rust proof steel plate for fuel tank having excellent press workability and corrosion resistance, and manufacture thereof |
| JPH11350099A (en) * | 1998-06-12 | 1999-12-21 | Nisshin Steel Co Ltd | Manufacture of aluminum plated steel sheet excellent in darkish discoloration resistance and workability |
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09156027A (en) * | 1995-12-08 | 1997-06-17 | Nippon Steel Corp | Rust proof steel plate for fuel tank having excellent press workability and corrosion resistance, and manufacture thereof |
| JPH11350099A (en) * | 1998-06-12 | 1999-12-21 | Nisshin Steel Co Ltd | Manufacture of aluminum plated steel sheet excellent in darkish discoloration resistance and workability |
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| JP2006152427A (en) * | 2004-10-29 | 2006-06-15 | Sumitomo Metal Ind Ltd | Hot-pressed steel sheet member, manufacturing method therefor and steel sheet to be hot-pressed |
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| JP2008195999A (en) * | 2007-02-13 | 2008-08-28 | Jfe Steel Kk | Steel sheet for hot press, and method for producing the same |
| JP4616854B2 (en) * | 2007-03-13 | 2011-01-19 | 新日本製鐵株式会社 | Al plated steel sheet for hot pressing |
| JP2008223084A (en) * | 2007-03-13 | 2008-09-25 | Nippon Steel Corp | Al PLATED STEEL SHEET FOR HOT PRESSING |
| JP4616900B2 (en) * | 2008-05-27 | 2011-01-19 | 新日本製鐵株式会社 | High-strength automotive parts with excellent corrosion resistance after painting |
| JP2008285757A (en) * | 2008-05-27 | 2008-11-27 | Nippon Steel Corp | High-strength automobile component having excellent corrosion resistance after coating |
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