JP2014118628A - MOLTEN Al PLATED STEEL PLATE FOR HOT STAMP, METHOD OF PRODUCING THE SAME, AND HOT STAMP PRODUCT - Google Patents
MOLTEN Al PLATED STEEL PLATE FOR HOT STAMP, METHOD OF PRODUCING THE SAME, AND HOT STAMP PRODUCT Download PDFInfo
- Publication number
- JP2014118628A JP2014118628A JP2012277378A JP2012277378A JP2014118628A JP 2014118628 A JP2014118628 A JP 2014118628A JP 2012277378 A JP2012277378 A JP 2012277378A JP 2012277378 A JP2012277378 A JP 2012277378A JP 2014118628 A JP2014118628 A JP 2014118628A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- hot
- thickness
- steel plate
- plating
- 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.)
- Granted
Links
Images
Landscapes
- Coating With Molten Metal (AREA)
Abstract
Description
本発明は、ホットスタンプ用溶融Alめっき鋼板およびその製造方法ならびにホットスタンプ製品に関し、特にホットスタンプ後にホットスタンプ製品の母材鋼板に脱炭層やスケールが発生するのを抑制できるホットスタンプ用溶融Alめっき鋼板およびその製造方法、並びに、その鋼板を用いて製造したホットスタンプ製品に関する。 TECHNICAL FIELD The present invention relates to a hot stamped molten Al plated steel sheet, a manufacturing method thereof, and a hot stamped product, and more particularly, hot stamped molten Al plated that can suppress the occurrence of a decarburized layer or scale on a base steel plate of a hot stamped product after hot stamping. The present invention relates to a steel plate, a manufacturing method thereof, and a hot stamp product manufactured using the steel plate.
近年、自動車用鋼板の用途(例えば、自動車のピラー、ドアインパクトビーム、バンパービーム等)などにおいて、高強度と高成形性を両立する鋼板が望まれており、これに対応するものの1つとして、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(Transformation Induced Plasticity)鋼がある。このTRIP鋼により、成形性の優れた1000MPa級程度の強度を有する高強度鋼板を製造することは可能であるが、さらに高強度、例えば1500MPa以上といった超高強度鋼で成形性を確保することは困難である。このような状況で、高強度及び高成形性を両立するものとして最近注目を浴びているのが、ホットスタンプ(熱間プレス、ホットスタンプ、ダイクエンチ、プレスクエンチ等とも呼称される。)である。このホットスタンプは、鋼板を800℃以上のオーステナイト域で加熱した後に熱間で成形することにより高強度鋼板の成形性を向上させ、成形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。 In recent years, in steel plate applications for automobiles (for example, automobile pillars, door impact beams, bumper beams, etc.) and the like, steel plates that have both high strength and high formability have been desired. There is TRIP (Transformation Induced Plasticity) steel using martensitic transformation of retained austenite. With this TRIP steel, it is possible to produce a high-strength steel sheet having excellent formability and a strength of about 1000 MPa, but it is possible to secure formability with ultra-high-strength steel having higher strength, for example, 1500 MPa or more. Have difficulty. Under such circumstances, hot stamping (also referred to as hot pressing, hot stamping, die quenching, press quenching, etc.) has recently attracted attention as being compatible with both high strength and high formability. This hot stamping improves the formability of a high-strength steel sheet by heating it in an austenite region at 800 ° C. or higher and then forming it hot, and it is baked by cooling after forming to obtain a desired material. It is.
ホットスタンプは、超高強度の部材を成形する方法として有望であるが、通常は大気中で鋼板を加熱する工程を有しており、この際、鋼板表面に酸化物(スケール)が生成するため、スケールを除去する工程が必要であった。ところが、このような後工程には、スケールの除去能や環境負荷等の観点からの対応策の必要性等の問題があった。 Hot stamping is promising as a method for forming ultra-high strength members, but usually has a step of heating a steel plate in the atmosphere, and at this time, oxide (scale) is generated on the surface of the steel plate. The process of removing the scale was necessary. However, such post-processes have problems such as the necessity of countermeasures from the viewpoints of scale removal ability and environmental load.
これを改善する技術として、ホットスタンプ用の鋼板としてAlめっき鋼板を使用することにより、加熱時のスケールの生成を抑制する技術が提案されている(例えば、特許文献1、2を参照)。 As a technique for improving this, a technique for suppressing the generation of scale during heating by using an Al-plated steel sheet as a hot stamping steel sheet has been proposed (for example, see Patent Documents 1 and 2).
ところが、ホットスタンプのために、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い材料であり、加工時に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するため、塗装後耐食性が低下するという問題があった。この問題を回避するには、この金属間化合物中にMnを添加する技術が提案されている(例えば、特許文献3を参照)が、ホットスタンプ製品の母材鋼板に脱炭層やスケールが発生するのを抑制する技術ではない。 However, due to hot stamping, the aluminum plating layer after local rapid heating has changed to an intermetallic compound up to the surface, and this compound is a very brittle material and is prone to cracking during processing. There is a drawback, and after severe molding, corrosion starts from these cracks, and there is a problem that the corrosion resistance after coating is lowered. In order to avoid this problem, a technique of adding Mn to the intermetallic compound has been proposed (see, for example, Patent Document 3). However, a decarburized layer and a scale are generated on the base steel plate of the hot stamp product. It is not a technology to suppress this.
本発明者らは、ホットスタンプ製品のAlめっき層に生じる微小なクラックを抑制することについて鋭意研究を進めたしたところ、溶融Alめっき鋼板のめっき層にクラックがあるとホットスタンプ前の加熱で雰囲気中の酸素や水蒸気がクラックから侵入し、母材鋼板に脱炭層やスケールが形成されることにより、ホットスタンプ製品の溶接性や耐食性を劣化させると共に、最表面に硬度不良が生じるという問題があることを新たに見出した。 The inventors of the present invention have intensively studied to suppress micro cracks generated in the Al plating layer of hot stamped products. Oxygen and water vapor invades from cracks, and a decarburized layer and scale are formed on the base steel plate, thereby deteriorating the weldability and corrosion resistance of hot stamped products and causing a problem of hardness failure on the outermost surface. I found a new thing.
そこで、本発明は、ホットスタンプ製品の母材鋼板に脱炭層やスケールが生成することを抑制することが出来る溶融Alめっき鋼板およびその製造方法、ならびに母材鋼板に脱炭層やスケールの生成することを抑制したホットスタンプ製品を提供することを課題とする。 Accordingly, the present invention provides a molten Al-plated steel sheet that can suppress the formation of a decarburized layer and scale on the base steel sheet of a hot stamp product, and a method for producing the same, and the generation of a decarburized layer and scale on the base steel sheet It is an object of the present invention to provide a hot stamp product that suppresses the above.
本発明者らは、上記課題を解決すべく、ホットスタンプ製品の母材鋼板に脱炭層やスケールが生成するのを抑制することについて鋭意研究をした、その結果、ホットスタンプ前の溶融Alめっき鋼板のめっき層と母材鋼板との間に生成する金属間化合物層の厚み、および金属間化合物層でないAl−Si層のめっき厚みを制限し、かつ金属間化合物層へのC方向のクラック幅を制限した溶融Alめっき鋼板を用いてホットスタンプすると、ホットスタンプ製品の母材鋼板に脱炭層やスケールが生成することを抑制できることを見出し、本発明を完成した。 In order to solve the above-mentioned problems, the present inventors have intensively studied to suppress the formation of a decarburized layer and scale on a base steel plate of a hot stamped product. The thickness of the intermetallic compound layer formed between the plating layer and the base steel sheet and the plating thickness of the Al—Si layer that is not the intermetallic compound layer are limited, and the crack width in the C direction to the intermetallic compound layer is limited. It has been found that when hot stamping is performed using a limited hot-dip Al-plated steel sheet, it is possible to suppress the formation of a decarburized layer and scale on the base steel sheet of the hot stamp product, and the present invention has been completed.
本発明の要旨は、次の通りである。 The gist of the present invention is as follows.
(1) 母材鋼板とめっき層との境界面に3〜12μm厚みのFe−Al−Si金属間化合物層および該金属間化合物層上に8〜50μm厚みのAl−Siめっき層を有するホットスタンプ用溶融Alめっき鋼板であって、前記金属間化合物層厚みが3〜7μmの場合には、該金属間化合物層のC方向のクラック幅が0.6μm以下、かつAl−Siめっき層の厚みが8〜50μmであり、前記金属間化合物層厚みが7超〜12μmの場合には、該金属間化合物層のC方向のクラック幅が1μm未満、かつAl−Siめっき層の厚みが14〜50μmであることを特徴とするホットスタンプ用溶融Alめっき鋼板。 (1) Hot stamping having an Fe—Al—Si intermetallic compound layer having a thickness of 3 to 12 μm on the interface between the base steel plate and the plating layer and an Al—Si plating layer having an thickness of 8 to 50 μm on the intermetallic compound layer When the thickness of the intermetallic compound layer is 3 to 7 μm, the crack width in the C direction of the intermetallic compound layer is 0.6 μm or less, and the thickness of the Al—Si plating layer is When the intermetallic compound layer thickness is more than 7 to 12 μm, the crack width in the C direction of the intermetallic compound layer is less than 1 μm, and the thickness of the Al—Si plating layer is 14 to 50 μm. A hot-stamped hot-dip galvanized steel sheet characterized by the following.
(2) 鋼板を溶融Alめっきするに当り、浴温が620〜675℃のAl−Siめっき浴に、浴内への浸漬時間が5〜10秒、侵入板温が浴温±20℃の条件で溶融Alめっきした後、圧下率0.5%未満のスキンパス圧延を行なうことを特徴とする上記(1)に記載のホットスタンプ用溶融Alめっき鋼板の製造方法。 (2) In hot dip Al plating of a steel sheet, a bath temperature of 620 to 675 ° C. is immersed in the bath for 5 to 10 seconds, and the penetration plate temperature is bath temperature ± 20 ° C. The hot-stamped molten Al-plated steel sheet according to the above (1), which is subjected to skin pass rolling with a rolling reduction of less than 0.5% after hot-dip aluminum plating.
(3)上記(1)に記載のホットスタンプ用溶融Alめっき鋼板を用いてホットスタンプしたホットスタンプ製品であって、ホットスタンプ製品の母材鋼板表層に形成された脱炭層の厚みが1μm未満であることを特徴とするホットスタンプ製品。 (3) A hot stamped product hot stamped using the hot stamped molten Al-plated steel sheet according to (1), wherein the thickness of the decarburized layer formed on the base steel sheet surface layer of the hot stamped product is less than 1 μm. A hot stamping product characterized by being.
本発明によれば、ホットスタンプ製品用の母材鋼板に脱炭層やスケールが生成することを抑制したので、溶接性、耐食性にすぐれ、表面性状に優れたホットスタンプ製品を得ることができる。 According to the present invention, since the formation of a decarburized layer or scale on the base steel plate for hot stamp products is suppressed, a hot stamp product excellent in weldability and corrosion resistance and having excellent surface properties can be obtained.
以下本発明を詳細に説明する。 The present invention will be described in detail below.
本発明に係るホットスタンプ用めっき鋼板は、鋼板表面に溶融Alめっきが施されたAlめっき鋼板であって、鋼材表面に形成される溶融Alめっき層は、その組成が質量%で、Al:80〜95%、Si:5〜15%からなるAlめっき層と鋼板の境界面に金属間化合物層(以降合金層と称する)であるFe−Al−Si層が形成されている。Fe−Al−Si合金層の組成は、通常Al:35〜65%、Si:5〜15%、残部はFeおよび不可避不純物からなる。 The plated steel sheet for hot stamping according to the present invention is an Al-plated steel sheet having a surface of the steel sheet subjected to hot-dip Al plating, and the hot-aluminum plated layer formed on the surface of the steel material has a composition of mass%, Al: 80 An Fe-Al-Si layer, which is an intermetallic compound layer (hereinafter referred to as an alloy layer), is formed at the boundary surface between the Al plating layer and the steel plate, which is composed of -95% and Si: 5-15%. The composition of the Fe—Al—Si alloy layer is usually Al: 35 to 65%, Si: 5 to 15%, and the balance consists of Fe and inevitable impurities.
この溶融Alめっきの組成および合金層の組成は公知のものである。この合金層は一般に極めて硬質でかつ脆性であるために加工した場合にクラックが生じ破壊の起点となり、かつこの起点よりAlめっき層の割れが惹き起こされる。ひどい場合は、めっき後のスキンパス圧延やレベラーをかけた時に割れるものがある。また、ホットスタンプ前の加熱をすると母材鋼板にスケールが発生したり、加熱後のホットスタンプ時に合金層にクラックが発生し、このクラックを起点としてAlめっき層の割れが惹き起こされたりことがある。 The composition of the molten Al plating and the composition of the alloy layer are known. Since this alloy layer is generally extremely hard and brittle, when it is processed, a crack is generated and becomes the starting point of fracture, and the crack of the Al plating layer is caused from this starting point. In severe cases, some may crack when subjected to skin pass rolling or leveler after plating. Also, heating before hot stamping may cause scale in the base steel sheet, or cracks in the alloy layer during hot stamping after heating, and the cracking of the Al plating layer may be caused from this crack. is there.
そして、このようなクラックが母材鋼板まで貫通して発生すると、クラックにより露出した母材鋼板は腐食の際のカソードとして作用するため腐食起点として作用し、まためっき割れに沿って腐食が伝播するため耐食性が著しく劣化する。さらに、本発明者らは、ホットスタンプ前の加熱で雰囲気中の酸素や水蒸気がクラックから侵入し、母材鋼板に脱炭層やスケールが形成される。例えば、図1の脱炭層(脱炭層硬度:ビッカース硬度260)が生成したときの断面組織の顕微鏡写真に示すように、母材鋼板に脱炭層やスケールが形成されて、ホットスタンプ製品の溶接性や耐食性を劣化させると共に、最表面に硬度不良が生じるという問題があることを新たに見出した。 And when such a crack penetrates to the base material steel plate, the base material steel plate exposed by the crack acts as a cathode at the time of corrosion, so it acts as a corrosion starting point, and corrosion propagates along the plating crack. Therefore, the corrosion resistance is significantly deteriorated. Furthermore, the present inventors have introduced oxygen and water vapor in the atmosphere from cracks by heating before hot stamping, and a decarburized layer and scale are formed on the base steel plate. For example, as shown in the micrograph of the cross-sectional structure when the decarburized layer (decarburized layer hardness: Vickers hardness 260) in FIG. 1 is generated, a decarburized layer and a scale are formed on the base steel plate, and the weldability of the hot stamping product It has been newly found that there is a problem that the corrosion resistance is deteriorated and the hardness is poor on the outermost surface.
そして、本発明者らは、ホットスタンプ製品の母材鋼板に生じる脱炭層やスケールを抑制するためには、ホットスタンプ用溶融Alめっき鋼板のめっき層のAl−Si層とFe−Al−Si合金層の厚さを所定の厚み以下に制限し、所定の圧下率以下のスキンパス圧延をして製造した溶融Alめっき鋼板を用いてホットスタンプすれば、製造されたホットスタンプ製品の母材鋼板に形成される脱炭層やスケールを抑制できることを見出し、本発明をなした。 And in order to suppress the decarburization layer and scale which arise in the base material steel plate of a hot stamp product, the present inventors are the Al-Si layer and the Fe-Al-Si alloy of the plating layer of the hot-dip hot-dip galvanized steel plate. If the hot stamping is performed using a hot-dip Al-plated steel sheet manufactured by skin pass rolling with the layer thickness limited to a predetermined thickness or less and a skin pass rolling of a predetermined reduction ratio or less, it is formed on the base steel sheet of the manufactured hot stamp product. The present invention has been made by finding that the decarburized layer and the scale can be suppressed.
図2は、ホットスタンプ用溶融Alめっき鋼板の合金層厚(μm)と合金層を除くAl−Si層の厚み(μm)及びホットスタンプ製品のスケール評点との関係を示す図である。 FIG. 2 is a diagram showing the relationship between the alloy layer thickness (μm) of the hot stamped molten Al-plated steel sheet, the thickness of the Al—Si layer excluding the alloy layer (μm), and the scale score of the hot stamp product.
スケール評点は、下記表1に示すようにめっき層内スケールを100倍の顕微鏡組織観察により、それらの発生状況によって評点付けをした。表1に示すように、スケール評点0、1は良好であるが、スケール評点2、3ではスケール発生が広範囲で、脱炭層も生じている状態である。
As shown in Table 1 below, the scale score was determined according to the state of occurrence of the scale in the plating layer by observing the microscopic structure 100 times. As shown in Table 1, scale scores 0 and 1 are good, but scale scores 2 and 3 are in a state where scale generation is wide and decarburized layers are also generated.
図2に示すように、ホットスタンプ用溶融Alめっき鋼板の合金層厚が3〜7μm、好ましくは3〜6.5μm、合金層のクラック幅0.6μm以下ではAl−Si層厚が8μm以上でないとホットスタンプ製品に評点2(◇)のスケール、脱炭層が発生し好ましくない。また、合金層厚が7超〜12μm、合金層のクラック幅1μm未満ではAl−Si層厚14μm以上でないと評点2(◇)のスケール、脱炭層の発生の懸念がある。図2中において、評点0(めっき層内スケールなし)を○、評点1を□、評点2を◇、そして、評点3を△で示している。 As shown in FIG. 2, the Al-Si layer thickness is not 8 μm or more when the alloy layer thickness of the hot stamped molten Al-plated steel sheet is 3 to 7 μm, preferably 3 to 6.5 μm, and the crack width of the alloy layer is 0.6 μm or less. The scale and decarburized layer of grade 2 (◇) are generated in hot stamped products, which is not preferable. Further, when the alloy layer thickness is more than 7 to 12 μm and the crack width of the alloy layer is less than 1 μm, the scale of grade 2 (◇) and the occurrence of a decarburized layer may occur unless the Al—Si layer thickness is 14 μm or more. In FIG. 2, a score 0 (no scale in the plating layer) is indicated by ◯, a score 1 is indicated by □, a score 2 is indicated by ◇, and a score 3 is indicated by Δ.
なお、合金層の上部に存在するAl−Si層の厚みの上限は、特に限定するものではないが、厚すぎるとホットスタンプの加熱時に合金化させるために長時間が必要となることからAl−Si層の厚みの上限を50μmとした。また、合金層厚およびAl−Si層厚はめっき鋼板の断面から光学顕微鏡や走査型電子顕微鏡等を用いて測定することができる。 The upper limit of the thickness of the Al—Si layer present on the upper part of the alloy layer is not particularly limited. However, if it is too thick, a long time is required for alloying when the hot stamp is heated. The upper limit of the thickness of the Si layer was 50 μm. The alloy layer thickness and the Al—Si layer thickness can be measured from the cross section of the plated steel sheet using an optical microscope, a scanning electron microscope, or the like.
したがって、本発明では、ホットスタンプ製品の母材鋼板に脱炭層やスケールが生成することを抑制することができるようにするために、ホットスタンプ用溶融Alめっき鋼板の合金層厚みが3〜7μm、かつ合金層でないAl−Si層の厚みが8〜50μm、または、合金層厚みが7超〜12μm、かつ合金層でないAl−Si層の厚みが14〜50μmとした。 Therefore, in the present invention, in order to be able to suppress the formation of a decarburized layer and scale on the base material steel plate of the hot stamp product, the alloy layer thickness of the hot stamped molten Al plated steel plate is 3 to 7 μm, The thickness of the Al—Si layer that is not an alloy layer is 8 to 50 μm, the thickness of the alloy layer is more than 7 to 12 μm, and the thickness of the Al—Si layer that is not an alloy layer is 14 to 50 μm.
本発明では、ホットスタンプ用めっき鋼板の鋼板成分は特に限定するものではないが、ホットスタンプ製品では金型を用いてプレスと焼入を同時に行い引張強さ:780MPa以上の高強度とするもので、焼入れ性に富む組成を有する鋼板とすることが好ましく、鋼中C量を質量%で0.15〜0.4%の水準となる。C量が0.15%未満では十分な焼入れ強度が得られず、また、C量が0.4質量%を超えると鋼板の靭性の低下が著しくなる。したがって、本発明では鋼中C量0.15〜0.4質量%の高強度鋼板であれば用いることができる。 In the present invention, the steel plate component of the hot stamped steel plate is not particularly limited, but in a hot stamp product, a mold is used to simultaneously press and quench to obtain a high strength of 780 MPa or more. It is preferable to use a steel plate having a composition rich in hardenability, and the amount of C in the steel is 0.15 to 0.4% by mass. When the C content is less than 0.15%, sufficient quenching strength cannot be obtained, and when the C content exceeds 0.4 mass%, the toughness of the steel sheet is significantly reduced. Therefore, in the present invention, any high-strength steel sheet having a C content in the steel of 0.15 to 0.4 mass% can be used.
このような鋼板としては、例えば、質量%で、C:0.15〜0.4%、Si:0.3%以下、Mn:0.8〜1.55%、Cr:0.1〜0.5%、B:0.0015〜0.005%、Al:0.04%以下を含み、残部Feおよび不可避的不純物からなる組成を有する鋼板が例示できる。なお、必要に応じて、Ti、Nb、Mo、V、Ni、Cu、Wを1種または2種以上をそれぞれ0.05%以下含有してもよい。 As such a steel plate, for example, in mass%, C: 0.15 to 0.4%, Si: 0.3% or less, Mn: 0.8 to 1.55%, Cr: 0.1 to 0 A steel plate having a composition comprising 0.5%, B: 0.0015 to 0.005%, Al: 0.04% or less, and the balance of Fe and inevitable impurities can be exemplified. In addition, if necessary, Ti, Nb, Mo, V, Ni, Cu, and W may be contained alone or in combination of two or more, each 0.05% or less.
本発明でのホットスタンプでの加熱方式については特に限定するものではない。通常の炉加熱や輻射熱を用いる赤外線方式の加熱方式を使用することも可能であるが、昇温速度50℃/秒以上の急速加熱を行うことが可能な、通電加熱や高周波誘導加熱等の電気を用いる加熱方式を使用することも可能である。但しこのときには電磁気的な相互作用により溶融したAlが局部的に盛り上がる現象(寄り)が発生する可能性がある。昇温速度の上限は特に規定しないが、上記の通電加熱や高周波誘導加熱等の加熱方式を使用する場合には、その装置の性能上、300℃/秒程度が上限である。 There is no particular limitation on the heating method using the hot stamp in the present invention. Although it is possible to use a normal furnace heating or an infrared heating method using radiant heat, electrical heating such as energization heating or high-frequency induction heating, which can perform rapid heating at a heating rate of 50 ° C./second or more. It is also possible to use a heating method using. However, at this time, there is a possibility that a phenomenon in which the molten Al locally rises due to electromagnetic interaction (shift) occurs. The upper limit of the rate of temperature rise is not particularly specified, but when using the heating method such as the above-mentioned current heating or high frequency induction heating, the upper limit is about 300 ° C./second due to the performance of the apparatus.
また、この加熱工程において、最高到達板温を850℃以上とすることが好ましい。最高到達板温をこの温度とするのは、鋼板をオーステナイト域まで加熱するとともに、表面まで十分に合金化を進行させるためである。 Moreover, in this heating process, it is preferable that the maximum reached plate temperature is 850 ° C. or higher. The reason why the maximum attainable plate temperature is set to this temperature is that the steel plate is heated to the austenite region and the alloying is sufficiently advanced to the surface.
本発明では、ホットスタンプ後の脱炭層の厚みを1μm未満に限定する。ホットスタンプ後の脱炭層の厚みが1μm以上となると、最表面に硬度不良を生じさせ、疲労強度が低下する懸念があるためである。 In the present invention, the thickness of the decarburized layer after hot stamping is limited to less than 1 μm. This is because when the thickness of the decarburized layer after hot stamping is 1 μm or more, there is a concern that a hardness failure is caused on the outermost surface and the fatigue strength is lowered.
なお、本発明でいう脱炭層は、硬度(Hv)が350以下で母材鋼板表層(鋼板内)に生成する層と定義する。そして、脱炭層は、断面研磨後、3vol.%ナイタールエッチング後、観察することができる。本発明では、倍率100倍で3つの視野を観察し、スケール及び脱炭層の有無を判定後、脱炭層があるものについては、1000倍に拡大し、脱炭層の厚みを測定した。 The decarburized layer as used in the present invention is defined as a layer having a hardness (Hv) of 350 or less and formed on the base steel sheet surface layer (in the steel sheet). And a decarburized layer is 3 vol. It can be observed after% nital etching. In the present invention, three fields of view were observed at a magnification of 100, and after determining the presence or absence of a scale and a decarburized layer, those having a decarburized layer were magnified 1000 times and the thickness of the decarburized layer was measured.
ホットスタンプ製品の母材鋼板表層に生成する脱炭層の厚みを1μm以下とするためには、溶融Alめっき鋼板の合金層のC方向のクラック幅を制御することが好ましい。すなわち、合金層の厚みが3〜7μmの場合には、合金層のC方向のクラック幅が0.6μm以下、合金層厚みが7超〜12μmと厚い場合には、クラックの許容幅はより大きくなり、1μm未満とすることが好ましい。先述したように合金層は金属間化合物で延性に乏しいため母材にスキンパス等の加工を加えると合金層にクラックが生成する。一旦クラックが生成した後は、新たなクラックも生成するがそれよりも既に生成したクラックがその幅を広げる場合が多い。クラック幅が大きいと、ホットスタンプ時に当該クラックを起点として母材鋼板に発生する脱炭層やスケールが形成されやすくなる。
したがって、本発明では母材鋼板表層(鋼板内)に生成するC方向のクラック幅を合金層の厚みに応じて0.6μm以下、あるいは1μm未満とした。なお、クラック幅は、幅の最大値とする。
In order to make the thickness of the decarburized layer formed on the surface layer of the base steel plate of the hot stamp product 1 μm or less, it is preferable to control the crack width in the C direction of the alloy layer of the hot-dip Al-plated steel plate. That is, when the alloy layer thickness is 3 to 7 μm, the crack width in the C direction of the alloy layer is 0.6 μm or less, and when the alloy layer thickness is thicker than 7 to 12 μm, the allowable crack width is larger. It is preferable that the thickness is less than 1 μm. As described above, since the alloy layer is an intermetallic compound and has poor ductility, when the base material is processed such as a skin pass, cracks are generated in the alloy layer. Once a crack has been generated, a new crack is also generated, but the already generated crack often expands its width. When the crack width is large, a decarburized layer and scale generated in the base steel plate starting from the crack at the time of hot stamping are easily formed.
Therefore, in the present invention, the width of the crack in the C direction generated on the base steel sheet surface layer (inside the steel sheet) is set to 0.6 μm or less or less than 1 μm depending on the thickness of the alloy layer. The crack width is the maximum value of the width.
なお、クラック幅の測定は、溶融Alめっき鋼板のAl−Siめっき層を電解剥離等の手法で除去して合金層表面を電子顕微鏡で観察することで行う。観察視野において特定されたクラックの幅を計数する。観察像でクラックは線状に観察され、観察視野におけるクラック幅の最大のものを計測する。電解剥離は例えば3%NaOHと1%AlCl3・6H2O溶液を用い、電流密度20mA/cm2で定電流電解することによってできる。 The crack width is measured by removing the Al—Si plating layer of the molten Al-plated steel sheet by a method such as electrolytic peeling and observing the surface of the alloy layer with an electron microscope. The width of the crack specified in the observation field is counted. In the observation image, the crack is observed linearly, and the largest crack width in the observation visual field is measured. Electrolytic peeling can be performed by, for example, constant current electrolysis at a current density of 20 mA / cm 2 using 3% NaOH and 1% AlCl 3 .6H 2 O solution.
次に、本発明に係るホットスタンプ用溶融Alめっき鋼板の製造方法について説明する。 Next, the manufacturing method of the hot stamped hot-dip galvanized steel sheet according to the present invention will be described.
鋼板の熱延、冷延条件については特に限定せず、通常の製造条件で行うものとする。
本発明に係る溶融Alめっき鋼板の製造方法は、浴温が620〜675℃のAl−Siめっき浴に、浴内への浸漬時間が2〜10秒、侵入板温が浴温±20℃の条件で溶融Alめっきした後、圧下率0.5%未満のスキンパス圧延を行なうことによって製造する。
The hot rolling and cold rolling conditions of the steel sheet are not particularly limited, and are performed under normal manufacturing conditions.
The manufacturing method of the hot-dip Al-plated steel sheet according to the present invention is such that the bath temperature is 620 to 675 ° C. and the immersion time in the bath is 2 to 10 seconds, and the intrusion plate temperature is bath temperature ± 20 ° C. After hot-dip Al plating under the conditions, it is manufactured by performing skin pass rolling with a rolling reduction of less than 0.5%.
溶融Alめっき浴としては、Alに3質量%〜15質量%のSiを含有する浴組成のものを使用することができ、これに不可避的不純物のFe等が混入している。これ以外の添加元素として、Mn、Cr、Mg、Ti、Zn、Sb、Sn、Cu、Ni、Co、In、Bi、ミッシュメタル等があり得るが、めっき層がAlを主体とする限り、どの添加元素も適用可能である。浴中のSiはAlめっき時の合金層成長を抑制する働きがあり、合金層厚みを12μm以下とするためには3質量%以上のSiが必要である。一方、Si量が多すぎるとめっき層中に粗大結晶として晶出し、耐食性やめっきの加工性を阻害するので、Si量は15質量%以下であることが好ましい。 As the molten Al plating bath, a bath composition containing 3% to 15% by mass of Si in Al can be used, and inevitable impurities such as Fe are mixed therein. Other additive elements may be Mn, Cr, Mg, Ti, Zn, Sb, Sn, Cu, Ni, Co, In, Bi, Misch metal, etc., as long as the plating layer is mainly Al. Additive elements are also applicable. Si in the bath has a function of suppressing the growth of the alloy layer at the time of Al plating, and 3% by mass or more of Si is required to make the alloy layer thickness 12 μm or less. On the other hand, if the amount of Si is too large, it will crystallize out as coarse crystals in the plating layer and inhibit the corrosion resistance and the workability of plating, so the amount of Si is preferably 15% by mass or less.
溶融Alめっきの浴温は、めっき層中の合金層厚と密接な関係があり、浴温が高くなると合金層が厚くなる。合金層厚を12μm以下とするためには、浴温を675℃以下とする必要がある。そして、浴温の下限は浴組成の融点で定まり、620℃が下限である。浴の融点はAl−10%Siで約600℃である。620℃未満では浴内の温度バラツキを考慮すると部分的に凝固してしまうため操業ができない。したがって、本発明では浴温を620〜675℃とした。また、合金層厚は、めっき浴内への浸漬時間によっても影響を受けるので、合金層厚を3〜12μmとするためには浸漬時間が3〜10秒であることが好ましい。また、鋼板の侵入温度が低すぎるとAlめっき浴との反応性が損なわれ、高すぎると合金層が成長しやすくなるので、良好なめっき層を得るためには浴温と侵入板温がほぼ一致していることが好ましく、浸漬時間が3〜10秒でめっき不良がなく良好なめっき層を形成するためには、めっき浴への侵入板温を浴温±20℃とする必要がある。侵入板温が高すぎると浴内での反応が進行して合金層が厚く成長し、また低すぎると浴内で局部的に温度差がついてドロスと呼ばれるAl−Fe化合物が鋼板上に晶出して外観品位を損ない、程度によっては鋼板への押疵となる。したがって、合金層厚やめっき厚は、溶融Alめっきの浴温、めっき浴内への浸漬時間、鋼板の侵入温度によって調整をすることができる。 The bath temperature of the molten Al plating is closely related to the alloy layer thickness in the plating layer, and the alloy layer becomes thicker as the bath temperature becomes higher. In order to make the alloy layer thickness 12 μm or less, the bath temperature needs to be 675 ° C. or less. And the minimum of bath temperature is decided by melting | fusing point of a bath composition, and 620 degreeC is a minimum. The melting point of the bath is about 600 ° C. with Al-10% Si. If it is less than 620 ° C., the operation cannot be performed because it partially solidifies in consideration of temperature variation in the bath. Therefore, in the present invention, the bath temperature is set to 620 to 675 ° C. Moreover, since the alloy layer thickness is also affected by the immersion time in the plating bath, the immersion time is preferably 3 to 10 seconds in order to make the alloy layer thickness 3 to 12 μm. In addition, if the penetration temperature of the steel sheet is too low, the reactivity with the Al plating bath is impaired, and if it is too high, the alloy layer tends to grow. Therefore, in order to obtain a good plating layer, the bath temperature and the penetration plate temperature are almost the same. In order to form a good plating layer having no plating failure with an immersion time of 3 to 10 seconds, it is necessary to set the intrusion plate temperature to the plating bath to a bath temperature ± 20 ° C. If the penetration plate temperature is too high, the reaction proceeds in the bath and the alloy layer grows thick. If the penetration plate temperature is too low, a temperature difference locally occurs in the bath, and an Al-Fe compound called dross crystallizes on the steel plate. The appearance quality is impaired, and depending on the degree, the steel sheet is pressed. Therefore, the alloy layer thickness and the plating thickness can be adjusted by the bath temperature of the molten Al plating, the immersion time in the plating bath, and the penetration temperature of the steel plate.
また、溶融Alめっき後には、鋼板の形状矯正や表面平滑性を確保するために、従来と同様なスキンパス圧延(調質圧延)を実施することが望ましい。そして、その際の圧下率は0.5%未満とする。圧下率が0.5%以上となると一旦生成したクラック部位へ応力集中し、合金層のC方向クラック幅が1μmを超えて大きくなりやすく、圧下率が低く、合金厚みが薄い方が合金層のC方向クラック幅を小さくすることができる。合金層のC方向クラック幅が大きくなると、続く加熱工程においてその部位より雰囲気中の酸素や水蒸気が侵入し、母材鋼板に脱炭層やスケールが形成されることとなる。したがって、スキンパス圧下率は0.5%未満とするが0.4%以下とすることが好ましい。さらに好ましくは0.3%以下である。なお、圧下率の下限は特に限定する必要がないものであるが、0.05%以上とすることが好ましい。 Moreover, after hot-dip Al plating, in order to ensure the shape correction and surface smoothness of the steel sheet, it is desirable to perform the same skin pass rolling (temper rolling) as before. And the rolling reduction in that case shall be less than 0.5%. When the rolling reduction is 0.5% or more, stress concentrates on the crack site once generated, the C-direction crack width of the alloy layer tends to increase beyond 1 μm, the rolling reduction is lower, and the alloy thickness is thinner. C direction crack width can be reduced. When the C-direction crack width of the alloy layer increases, oxygen and water vapor in the atmosphere enter from the site in the subsequent heating step, and a decarburized layer and scale are formed on the base steel plate. Therefore, the skin pass reduction ratio is less than 0.5%, but is preferably 0.4% or less. More preferably, it is 0.3% or less. The lower limit of the rolling reduction is not particularly limited, but is preferably 0.05% or more.
以下実施例に基づいて本発明を詳細に説明する。
質量%で、C:0.23%、Si:0.21%、Mn:1.2%、P:0.01%、S:0.003%、Cr:0.2%、B:0.0027%、Al:0.03%、Ti:0.03%を含有し、残部がFeおよび不可避的不純物からなる成分を有する板厚1.6mmの冷延鋼板を用いて溶融Al−Siめっきを施した。Si濃度9質量%とし、浴温、侵入板温及び浸漬時間を変更することで種々の合金層厚みとした。めっき浴から引き上げた後にN2ガスワイピングを行うことでAl−Siめっき付着量(Al−Si厚み)を調節し、その後スキンパス圧延を行なってホットスタンプ用溶融Alめっき鋼板を作製した。
Hereinafter, the present invention will be described in detail based on examples.
In mass%, C: 0.23%, Si: 0.21%, Mn: 1.2%, P: 0.01%, S: 0.003%, Cr: 0.2%, B: 0.0. Hot-dip Al-Si plating using a cold-rolled steel sheet having a thickness of 1.6 mm, containing 0027%, Al: 0.03%, Ti: 0.03%, with the balance being composed of Fe and inevitable impurities gave. The Si concentration was set to 9% by mass, and various alloy layer thicknesses were obtained by changing the bath temperature, the penetration plate temperature, and the immersion time. After lifting from the plating bath, N 2 gas wiping was performed to adjust the Al-Si plating adhesion amount (Al-Si thickness), and then skin pass rolling was performed to produce a hot stamped molten Al plated steel sheet.
この鋼板の合金層厚、Al−Si層厚(合金層厚を含まず)、C方向クラック幅を測定した。合金層厚、Al−Si層厚は、断面からの光学顕微鏡により、またクラック幅はAl−Si層を3%NaOH−1%AlCl3・6H2O中で定電流電解剥離することで合金層を露出させ、その表面を二次電子像5000倍で観察することで行った。 The alloy layer thickness, Al-Si layer thickness (not including the alloy layer thickness), and C-direction crack width of this steel plate were measured. Alloy layer thickness, Al-Si layer thickness, the optical microscope from the cross section, also cracks width alloy layer by constant current electrolytic stripping the Al-Si layer with 3% NaOH-1% AlCl 3 · 6H 2 O in Was exposed, and the surface was observed at a secondary electron image of 5000 times.
この鋼板をホットスタンプに相当する条件で処理した。大気中で電気炉内に挿入することで900℃に加熱した後に1分間保定し、約700℃の温度まで大気中で冷却して、その後、厚さ50mmの金型間で圧着することで急冷した。 This steel plate was processed under conditions corresponding to hot stamping. After being heated to 900 ° C by being inserted into an electric furnace in the atmosphere, held for 1 minute, cooled to a temperature of about 700 ° C in the atmosphere, and then rapidly cooled by pressure bonding between molds having a thickness of 50 mm. did.
上記の加熱−急冷処理を施した後に、めっき層の断面を観察した。断面研磨後、ナイタールでエッチングすることでめっき層−鋼板界面が観察され、鋼板の焼入組織も観察できる。このとき、図1に示すように、合金化しためっき層内部にスケール、つまりFeの酸化物が観察された。スケールが発生した部位の鋼板最表層には脱炭層も観察された。 After performing the heating-rapid cooling treatment, the cross section of the plating layer was observed. After the cross section polishing, the plating layer-steel plate interface is observed by etching with nital, and the quenched structure of the steel plate can also be observed. At this time, as shown in FIG. 1, a scale, that is, an oxide of Fe, was observed inside the alloyed plating layer. A decarburized layer was also observed on the outermost surface layer of the steel plate where the scale occurred.
浴温、進入板温、浸漬時間、めっき付着量を変えた時の合金層厚みとAl−Si層厚みを表2に示す。またスキンパス圧下率とスケール生成の評点も記載している。スケール評点は表1に示した基準である。
Table 2 shows the alloy layer thickness and the Al—Si layer thickness when the bath temperature, the approach plate temperature, the immersion time, and the amount of plating adhesion were changed. It also lists the skin pass reduction rate and the scale generation score. The scale score is the standard shown in Table 1.
表2に示すように、合金層厚みとAl−Si厚み及び合金層のクラック幅によりスケールの発生状と脱炭の状況が変化する。本発明例は、いずれもスケール評点は0、1と良好であった。 As shown in Table 2, the scale generation state and the decarburization state vary depending on the alloy layer thickness, the Al—Si thickness, and the crack width of the alloy layer. The inventive examples all had good scale scores of 0 and 1.
これに対して、番号9、14、19、24の比較例に示すようにAl−Si厚が5μmと非常に薄い場合、あるいは番号5〜7の比較例に示すようにAl−Si層が10μmと薄い(14μm未満)場合に合金層の厚みが8.5〜11.5μmの範囲で7μm超であると、スケールの発生を抑制できない(スケール評点2、3となっていた)。 On the other hand, when the Al—Si thickness is very thin as 5 μm as shown in the comparative examples of Nos. 9, 14, 19, and 24, or the Al—Si layer is 10 μm as shown in the comparative examples of Nos. 5-7. When the thickness of the alloy layer is less than 14 μm and the thickness of the alloy layer is more than 7 μm in the range of 8.5 to 11.5 μm, the generation of scale cannot be suppressed (the scale scores are 2 and 3).
また合金層の厚みが13μmと非常に厚い場合には番号8のようにAl−Si層が10μmと厚くてもスケール発生を抑制できない(スケール評点3となっていた)。 In addition, when the thickness of the alloy layer is 13 μm, even if the Al—Si layer is as thick as 10 μm as indicated by No. 8, scale generation cannot be suppressed (scale score 3).
スキンパスの圧下率が高い場合(番号36、37)や侵入板温が高い場合(番号38)にもスケールが発生しやすい。 Scale is also likely to occur when the skin pass reduction rate is high (Nos. 36 and 37) and the penetration plate temperature is high (No. 38).
以上の試験結果よりして、ホットスタンプ用溶融Alめっき鋼板の合金層の厚み、合金層のC方向のクラック幅、Al−Siめっき層の厚みの条件を適切に制御することによってホットスタンプ製品の母材鋼板に脱炭層やスケールの発生を抑制できることが分った。 Based on the above test results, by properly controlling the conditions of the alloy layer thickness of the hot stamped hot-dip galvanized steel sheet, the crack width in the C direction of the alloy layer, and the thickness of the Al-Si plating layer, It was found that generation of decarburized layers and scales on the base steel plate can be suppressed.
Claims (3)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2012277378A JP6056450B2 (en) | 2012-12-19 | 2012-12-19 | Hot stamped hot-dip galvanized steel sheet, manufacturing method thereof, and hot stamping product |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2012277378A JP6056450B2 (en) | 2012-12-19 | 2012-12-19 | Hot stamped hot-dip galvanized steel sheet, manufacturing method thereof, and hot stamping product |
Publications (2)
Publication Number | Publication Date |
---|---|
JP2014118628A true JP2014118628A (en) | 2014-06-30 |
JP6056450B2 JP6056450B2 (en) | 2017-01-11 |
Family
ID=51173721
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2012277378A Active JP6056450B2 (en) | 2012-12-19 | 2012-12-19 | Hot stamped hot-dip galvanized steel sheet, manufacturing method thereof, and hot stamping product |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP6056450B2 (en) |
Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2018142534A1 (en) * | 2017-02-02 | 2018-08-09 | 新日鐵住金株式会社 | ALLOYED-Al-PLATED STEEL SHEET FOR HOT STAMPING, AND HOT-STAMPED MEMBER |
JP6406475B1 (en) * | 2017-11-20 | 2018-10-17 | 新日鐵住金株式会社 | Al-plated welded pipe for quenching, Al-plated hollow member and method for producing the same |
CN110352259A (en) * | 2017-02-28 | 2019-10-18 | 塔塔钢铁艾默伊登有限责任公司 | The method for being used to prepare the steel band with aluminum alloy coating layer |
JP2020509203A (en) * | 2016-12-23 | 2020-03-26 | ポスコPosco | Hot-formed plated steel sheet excellent in impact characteristics, hot-formed member, and method for producing them |
JP2022522761A (en) * | 2019-03-29 | 2022-04-20 | 宝山鋼鉄股▲分▼有限公司 | Welded parts made of aluminum or steel with aluminum alloy plating layer with different strength and their manufacturing method |
WO2022215636A1 (en) * | 2021-04-06 | 2022-10-13 | 日本製鉄株式会社 | Steel sheet for hot stamping and hot-stamped member |
CN115522154A (en) * | 2022-10-09 | 2022-12-27 | 浙江吉利控股集团有限公司 | Stabilizer bar, preparation method thereof, suspension assembly and vehicle |
WO2024023690A1 (en) * | 2022-07-28 | 2024-02-01 | Arcelormittal | Automotive vehicle with press hardened visible steel parts |
WO2024023697A1 (en) * | 2022-07-28 | 2024-02-01 | Arcelormittal | Automotive vehicle with press hardened visible steel parts |
US12049678B2 (en) | 2016-12-23 | 2024-07-30 | Posco Co., Ltd | Plated steel sheet for hot press forming having excellent impact property, hot press formed part, and manufacturing method thereof |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH07188887A (en) * | 1993-12-28 | 1995-07-25 | Nippon Steel Corp | Hot dip aluminized steel sheet excellent in corrosion resistance |
JP2012126994A (en) * | 2010-11-26 | 2012-07-05 | Jfe Steel Corp | Al-Zn-BASED HOT-DIP PLATED STEEL SHEET |
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 |
-
2012
- 2012-12-19 JP JP2012277378A patent/JP6056450B2/en active Active
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH07188887A (en) * | 1993-12-28 | 1995-07-25 | Nippon Steel Corp | Hot dip aluminized steel sheet excellent in corrosion resistance |
JP2012126994A (en) * | 2010-11-26 | 2012-07-05 | Jfe Steel Corp | Al-Zn-BASED HOT-DIP PLATED STEEL SHEET |
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 |
Cited By (25)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US11274357B2 (en) | 2016-12-23 | 2022-03-15 | Posco | Plated steel sheet for hot press forming having excellent impact property, hot press formed part, and manufacturing method thereof |
US12049678B2 (en) | 2016-12-23 | 2024-07-30 | Posco Co., Ltd | Plated steel sheet for hot press forming having excellent impact property, hot press formed part, and manufacturing method thereof |
JP2020509203A (en) * | 2016-12-23 | 2020-03-26 | ポスコPosco | Hot-formed plated steel sheet excellent in impact characteristics, hot-formed member, and method for producing them |
US11732323B2 (en) | 2016-12-23 | 2023-08-22 | Posco | Plated steel sheet for hot press forming having excellent impact property, hot press formed part, and manufacturing method thereof |
US10934601B2 (en) | 2016-12-23 | 2021-03-02 | Posco | Plated steel sheet for hot press forming having excellent impact property, hot press formed part, and manufacturing method thereof |
WO2018142534A1 (en) * | 2017-02-02 | 2018-08-09 | 新日鐵住金株式会社 | ALLOYED-Al-PLATED STEEL SHEET FOR HOT STAMPING, AND HOT-STAMPED MEMBER |
CN110234781A (en) * | 2017-02-02 | 2019-09-13 | 日本制铁株式会社 | Drop stamping alloying Al-plated steel sheet and drop stamping component |
JPWO2018142534A1 (en) * | 2017-02-02 | 2019-11-14 | 日本製鉄株式会社 | Alloyed aluminum plated steel sheet for hot stamping and hot stamping member |
EP3578680A4 (en) * | 2017-02-02 | 2020-10-14 | Nippon Steel Corporation | ALLOYED-Al-PLATED STEEL SHEET FOR HOT STAMPING, AND HOT-STAMPED MEMBER |
CN110352259A (en) * | 2017-02-28 | 2019-10-18 | 塔塔钢铁艾默伊登有限责任公司 | The method for being used to prepare the steel band with aluminum alloy coating layer |
US11319623B2 (en) | 2017-02-28 | 2022-05-03 | Tata Steel Ijmuiden B.V. | Method for producing a steel strip with an aluminium alloy coating layer |
US11807924B2 (en) | 2017-11-20 | 2023-11-07 | Nippon Steel Corporation | Al plated welded pipe for hardening use and Al plated hollow member and method for producing same |
CN111247266B (en) * | 2017-11-20 | 2022-02-11 | 日本制铁株式会社 | Al-plated welded pipe for quenching, Al-plated hollow member, and method for producing same |
JP6406475B1 (en) * | 2017-11-20 | 2018-10-17 | 新日鐵住金株式会社 | Al-plated welded pipe for quenching, Al-plated hollow member and method for producing the same |
CN111247266A (en) * | 2017-11-20 | 2020-06-05 | 日本制铁株式会社 | Al-plated welded pipe for quenching, Al-plated hollow member, and method for producing same |
WO2019097729A1 (en) * | 2017-11-20 | 2019-05-23 | 日本製鉄株式会社 | Al-PLATED WELDED PIPE FOR HARDENING, Al-PLATED HOLLOW MEMBER, AND PRODUCTION METHOD THEREFOR |
JP2022522761A (en) * | 2019-03-29 | 2022-04-20 | 宝山鋼鉄股▲分▼有限公司 | Welded parts made of aluminum or steel with aluminum alloy plating layer with different strength and their manufacturing method |
JP7343603B2 (en) | 2019-03-29 | 2023-09-12 | 宝山鋼鉄股▲分▼有限公司 | Welded parts made of steel with aluminum or aluminum alloy plating layer that have different strengths and their manufacturing method |
WO2022215636A1 (en) * | 2021-04-06 | 2022-10-13 | 日本製鉄株式会社 | Steel sheet for hot stamping and hot-stamped member |
WO2024023697A1 (en) * | 2022-07-28 | 2024-02-01 | Arcelormittal | Automotive vehicle with press hardened visible steel parts |
WO2024023552A1 (en) * | 2022-07-28 | 2024-02-01 | Arcelormittal | Method for manufacturing a coated press hardened steel part having an improved appearance and corresponding steel part |
WO2024023690A1 (en) * | 2022-07-28 | 2024-02-01 | Arcelormittal | Automotive vehicle with press hardened visible steel parts |
WO2024023553A1 (en) * | 2022-07-28 | 2024-02-01 | Arcelormittal | Method for manufacturing a coated press hardened steel part having an improved appearance and corresponding steel part |
CN115522154B (en) * | 2022-10-09 | 2024-04-16 | 浙江吉利控股集团有限公司 | Stabilizer bar, preparation method thereof, suspension assembly and vehicle |
CN115522154A (en) * | 2022-10-09 | 2022-12-27 | 浙江吉利控股集团有限公司 | Stabilizer bar, preparation method thereof, suspension assembly and vehicle |
Also Published As
Publication number | Publication date |
---|---|
JP6056450B2 (en) | 2017-01-11 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP6056450B2 (en) | Hot stamped hot-dip galvanized steel sheet, manufacturing method thereof, and hot stamping product | |
JP5444650B2 (en) | Plated steel sheet for hot press and method for producing the same | |
JP5605503B2 (en) | Steel sheet for hot stamp member and manufacturing method thereof | |
JP5463906B2 (en) | Steel sheet for hot stamping and manufacturing method thereof | |
JP5817479B2 (en) | Manufacturing method of hot press member | |
JP4725415B2 (en) | Hot-pressed steel sheet, hot-pressed steel sheet member, and production method thereof | |
JP6719486B2 (en) | HPF molded member excellent in peeling resistance and method for manufacturing the same | |
JP5614496B2 (en) | Hot stamped high strength parts with excellent post-painting corrosion resistance and manufacturing method thereof | |
JP5825413B1 (en) | Manufacturing method of hot press-formed product | |
JP6475824B2 (en) | HPF molded member having excellent peel resistance and method for producing the same | |
JP6607338B1 (en) | Fe-Al plating hot stamp member and method for producing Fe-Al plating hot stamp member | |
JP6234845B2 (en) | High strength galvannealed steel sheet with excellent bake hardenability and bendability | |
JP6020589B2 (en) | Manufacturing method of hot press member | |
JP6269079B2 (en) | Steel sheet for hot stamping and manufacturing method thereof | |
JP2011231367A (en) | Hot dip galvanized steel sheet and method for producing the same | |
US11299793B2 (en) | Steel sheet having excellent resistance to liquid metal embrittlement cracks and method for manufacturing the same | |
JP7241283B2 (en) | Aluminum-iron plated steel sheet for hot press with excellent corrosion resistance and weldability and its manufacturing method | |
JP6152836B2 (en) | Manufacturing method of hot press-formed product | |
JP2010018856A (en) | High-strength automobile component excellent in corrosion resistance after coating, and plated steel sheet for hot press | |
KR20200066239A (en) | STEEL SHEET PLATED WITH Al-Fe FOR HOT PRESS FORMING HAVING EXCELLENT CORROSION RESISTANCE AND SPOT WELDABILITY, AND MANUFACTURING METHOD THEREOF | |
JP6379717B2 (en) | Method for producing alloyed hot-dip galvanized steel for hot stamping | |
KR20200066237A (en) | STEEL SHEET PLATED WITH Al FOR HOT PRESS FORMING HAVING IMPROVED RESISTANCE AGAINST HYDROGEN DELAYED FRACTURE AND SPOT WELDABILITY, AND MANUFACTURING METHOD THEREOF | |
JP6661772B2 (en) | Hot press-formed product in which fine cracks are suppressed and method for producing the same | |
JP2015168881A (en) | Hot pressing steel sheet | |
JP6237729B2 (en) | Steel sheet for hot press |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
RD02 | Notification of acceptance of power of attorney |
Free format text: JAPANESE INTERMEDIATE CODE: A7422 Effective date: 20150105 |
|
A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20150805 |
|
A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20160512 |
|
A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20160628 |
|
A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20160824 |
|
TRDD | Decision of grant or rejection written | ||
A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20161108 |
|
A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20161121 |
|
R151 | Written notification of patent or utility model registration |
Ref document number: 6056450 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R151 |
|
S533 | Written request for registration of change of name |
Free format text: JAPANESE INTERMEDIATE CODE: R313533 |
|
R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |