JP2003147499A - Steel sheet for hot press, and production method therefor - Google Patents
Steel sheet for hot press, and production method thereforInfo
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- JP2003147499A JP2003147499A JP2001342151A JP2001342151A JP2003147499A JP 2003147499 A JP2003147499 A JP 2003147499A JP 2001342151 A JP2001342151 A JP 2001342151A JP 2001342151 A JP2001342151 A JP 2001342151A JP 2003147499 A JP2003147499 A JP 2003147499A
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- steel sheet
- less
- hot
- steel
- dip galvanizing
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- Coating With Molten Metal (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、自動車のボデー構
造部品、足回り部品等を始めとする機械構造部品等の製
造に使用される熱間プレス用鋼板に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a hot-pressing steel sheet used for manufacturing mechanical structural parts such as body structural parts and suspension parts for automobiles.
【０００２】[0002]
【従来の技術】近年、自動車の軽量化のため、鋼材の高
強度化を図り、使用重量を減ずる努力が進んでいる。し
かし、自動車に広く使用される薄鋼板においては、鋼板
強度の増加に伴って、プレス成形性が低下し、複雑な形
状を製造することが困難になってきている。具体的に
は、延性が低下して加工度が高い部位で破断が生じる、
スプリングバックや壁反りが大きくなり寸法精度が劣化
するという問題が発生する。従って、高強度、特に780M
Pa級以上の鋼板を用いて、プレス成形で部品を製造する
ことは容易ではない。プレス成形ではなくロール成形に
よれば、高強度の鋼板の加工が可能であるが、長手方向
に一様な断面を有する部品にしか適用できない。2. Description of the Related Art In recent years, in order to reduce the weight of automobiles, efforts have been made to increase the strength of steel materials and reduce the weight used. However, in the case of thin steel sheets that are widely used in automobiles, the press formability decreases as the strength of the steel sheet increases, making it difficult to manufacture complex shapes. Specifically, fracture occurs at a site where ductility is reduced and workability is high,
There is a problem that the springback and the wall warp increase and the dimensional accuracy deteriorates. Therefore, high strength, especially 780M
It is not easy to manufacture parts by press molding using steel sheets of Pa grade or higher. High-strength steel plates can be processed by roll forming instead of press forming, but can be applied only to parts having a uniform cross section in the longitudinal direction.
【０００３】一方、英国公開特許公報1490535 で示され
ているように、加熱した鋼板をプレス成形する熱間プレ
スと呼ばれる方法では、鋼板が高温で軟質、高延性にな
っているため、複雑な形状を寸法精度よく成形すること
が可能である。さらに、鋼板をオーステナイト域に加熱
しておき、金型内で急冷することにより、マルテンサイ
ト変態による鋼板の高強度化が同時に達成できる。On the other hand, as disclosed in British Patent Publication No. 1490535, in a method called hot pressing for press-forming a heated steel sheet, the steel sheet is soft and has high ductility at high temperatures, and thus has a complicated shape. Can be molded with high dimensional accuracy. Further, by heating the steel sheet in the austenite region and quenching it in the mold, it is possible to simultaneously achieve high strength of the steel sheet by martensitic transformation.
【０００４】このように熱間プレスは優れた成形方法で
あるが、800 〜1000℃といった高温に加熱することが必
要なため、鋼板表面が酸化するという問題が生じる。こ
のとき生じる鉄酸化物からなるスケールがプレス時に脱
落して金型に付着して生産性が低下したり、あるいはプ
レス後の製品にそのようなスケールが残存して外観が不
良となるという問題がある。しかも、このようなスケー
ルが製品に残存すると、次工程で塗装する場合に鋼板と
塗膜の密着性が劣り、耐食性の低下を招く。そこで熱間
プレス成形後は、ショットブラスト等のスケール除去処
理が必要となり、コスト増は免れない。また加熱時にそ
のようなスケールを形成させないために合金鋼やステン
レス鋼を用いても、スケール発生は完全に防止できない
ばかりか、普通鋼に比較し大幅なコスト増となる。また
加熱時の雰囲気とプレス工程全体を非酸化性雰囲気にす
ることも理論的に有効であるが、設備上大幅なコスト増
になる。As described above, hot pressing is an excellent forming method, but since it needs to be heated to a high temperature of 800 to 1000 ° C., it causes a problem that the surface of the steel sheet is oxidized. There is a problem that the scale made of iron oxide generated at this time falls off during press and adheres to the mold to reduce productivity, or such scale remains in the product after pressing and the appearance becomes poor. is there. Moreover, if such scale remains in the product, the adhesion between the steel sheet and the coating film will be poor in the case of coating in the next step, and the corrosion resistance will be reduced. Therefore, after hot press molding, scale removal processing such as shot blasting is required, which inevitably increases costs. Further, even if alloy steel or stainless steel is used to prevent the formation of such a scale during heating, the scale generation cannot be completely prevented, and the cost is greatly increased as compared with the ordinary steel. In addition, it is theoretically effective to make the atmosphere during heating and the non-oxidizing atmosphere the entire pressing process, but the cost is significantly increased in terms of equipment.
【０００５】このような問題を解決すべく、特開2000−
38640 号公報では、熱間成形時に耐酸化抵抗性を持たせ
るためにアルミニウム被覆した鋼板を提案しているが、
このような鋼板も普通鋼と比較した場合、大幅なコスト
増となる。In order to solve such a problem, Japanese Patent Laid-Open No. 2000-
Japanese Patent No. 38640 proposes a steel sheet coated with aluminum in order to have oxidation resistance during hot forming.
Such a steel sheet also has a large cost increase as compared with ordinary steel.
【０００６】このような事情から、今日でも熱間プレス
が十分に活用されていないのが現状である。特開2000−
144238号公報および特開2000−248338号公報には、常法
により成形した部品の一部を、高周波誘導加熱した後に
急冷し、鋼板を変態強化させる技術が開示されている。
これらは、防錆のために亜鉛系被膜を有する鋼板を用い
ているが、加熱による亜鉛の消散を抑制するため、加熱
温度を850 ℃以下にしたり、加熱時間を短時間にすると
いう制約がある。850 ℃以下の加熱では、オーステナイ
ト単相にならないため、焼入後のマルテンサイト体積率
が少なくなり、高強度が得られない。短時間の加熱で
は、セメンタイトが完全に溶解できなくて固溶炭素が少
なくなり、焼入後の強度が不足するという問題も考えら
れる。Under these circumstances, the hot press is not fully utilized even today. JP 2000-
Japanese Patent Laid-Open No. 144238 and Japanese Patent Laid-Open No. 2000-248338 disclose a technique of transforming and strengthening a steel sheet by high-frequency induction heating and then rapidly cooling a part of a component formed by a conventional method.
These use a steel sheet with a zinc-based coating for rust prevention, but to suppress the dissipation of zinc by heating, there are restrictions such as heating temperature below 850 ° C and shortening the heating time. . When heated below 850 ° C, the austenite single phase does not occur, so the volume ratio of martensite after quenching decreases and high strength cannot be obtained. When heated for a short time, cementite may not be completely dissolved and solid solution carbon may be reduced, resulting in insufficient strength after quenching.
【０００７】これらの技術を熱間プレスに適用すること
を考えると、短時間で加熱、急冷を行うことは設備的に
困難をともなう。さらに、高温で加工を受けたときの、
皮膜の損傷については不明である。したがって、これら
の技術をそのまま熱間プレスに転用しても、高強度かつ
耐食性に優れた部材を得ることは難しい。Considering the application of these techniques to a hot press, it is difficult to perform heating and quenching in a short time in terms of equipment. Furthermore, when processed at high temperature,
The damage to the coating is unknown. Therefore, even if these techniques are directly applied to hot pressing, it is difficult to obtain a member having high strength and excellent corrosion resistance.
【０００８】[0008]
【発明が解決しようとする課題】本発明の課題は、熱間
プレス法により高強度部品が製造でき、かつスケール生
成抑制のために特段の工程や設備を増やすことなく成形
後の耐食性も確保できる、安価な熱間プレス用鋼板とそ
の製造方法を提供することである。The object of the present invention is to produce a high-strength part by the hot pressing method and to secure corrosion resistance after molding without increasing special steps or facilities for suppressing scale formation. It is an object of the present invention to provide an inexpensive steel plate for hot pressing and a manufacturing method thereof.
【０００９】[0009]
【課題を解決するための手段】本発明者らは、鋼板の表
面処理によってスケール生成を防止すべく鋭意検討の結
果、Zn−Fe合金皮膜の存在がスケール防止に有効である
との知見を得た。Means for Solving the Problems The present inventors have conducted extensive studies to prevent scale formation by surface treatment of steel sheets, and as a result, have found that the presence of a Zn--Fe alloy coating is effective for scale prevention. It was
【００１０】一般にこれらの合金相の融点は約800 ℃以
下であるため、熱間プレスに必要な800 〜1000℃という
温度に加熱するとZn−Fe合金被膜層（以後、めっき層と
呼称する）が溶融して表面より蒸発・消失し、熱間プレ
スに有害な鉄系酸化物からなるスケール（以後、単にス
ケールと呼称する）が発生すると考えられた。Generally, since the melting points of these alloy phases are about 800 ° C. or less, when heated to a temperature of 800 to 1000 ° C. necessary for hot pressing, a Zn-Fe alloy coating layer (hereinafter referred to as a plating layer) is formed. It is considered that the molten metal evaporates and disappears from the surface, and scales (hereinafter simply referred to as scales) composed of iron oxides that are harmful to hot pressing are generated.
【００１１】しかし、本発明者らは、予想外にも、めっ
き層の初期Fe質量％、つまりめっき層のFe含有量および
めっき付着量を適正化することにより、めっき層の蒸発
・消失を防止し、同時にスケール生成が抑制されること
を見い出した。そのメカニズムは次のように考えられ
た。However, the present inventors unexpectedly prevent the evaporation / disappearance of the plating layer by optimizing the initial Fe mass% of the plating layer, that is, the Fe content and the coating adhesion amount of the plating layer. At the same time, they found that scale generation was suppressed. The mechanism was considered as follows.
【００１２】適正化されためっき層を有する鋼板を加熱
すると、めっき層表面にZnO 層が加熱段階で全面に形成
されるためZnの蒸発が抑制される。また素地鋼板とめっ
き層の間でFeとZnの相互拡散が起こり、その結果、めっ
き層中のFe質量％が増加して、Fe-Zn 合金層が形成され
る。つまり、適正化されためっき層を有する鋼板を加熱
すると、表面から順にZnO 層、Fe-Zn 合金層、素地鋼板
の３層構造が得られ、熱間プレスに有害なスケールは形
成されない。When a steel sheet having an optimized plating layer is heated, a ZnO layer is formed on the entire surface of the plating layer during the heating step, so that evaporation of Zn is suppressed. Further, interdiffusion of Fe and Zn occurs between the base steel sheet and the plating layer, and as a result, the mass% of Fe in the plating layer increases, and the Fe-Zn alloy layer is formed. That is, when a steel sheet having an optimized plating layer is heated, a three-layer structure of a ZnO layer, an Fe-Zn alloy layer, and a base steel sheet is obtained in order from the surface, and no harmful scale is formed in hot pressing.
【００１３】このZnO 層が表面に全面形成されるまで
は、ZnO 層形成とZn蒸発が競合するため、めっき層の初
期Fe質量％が低くて融点が低い場合には、FeとZnの相互
拡散が十分進まずZnの蒸気圧が高くなるためZnO 層が全
面に形成される前にZnが蒸発し、スケール生成が抑制で
きない。一方、めっき層の初期Fe質量％が高い場合に
は、ZnO 層が全面に形成されづらくなり、下層のFe−Zn
合金層が酸化され、スケールが生成しやすくなる。また
めっき付着量が少ない場合には、ZnO 層が十分に形成さ
れないためスケール発生が抑制されず、めっき付着量が
多い場合には、ZnO層は十分に形成されるが、FeとZnの
相互拡散が十分進まず溶融亜鉛層が残存するため、プレ
ス時に金型が汚染される。Until the ZnO layer is entirely formed on the surface, the ZnO layer formation and the Zn evaporation compete with each other. Therefore, when the initial Fe mass% of the plating layer is low and the melting point is low, the interdiffusion of Fe and Zn occurs. However, since the vapor pressure of Zn does not progress sufficiently and Zn vaporizes before the ZnO layer is formed on the entire surface, scale formation cannot be suppressed. On the other hand, when the initial Fe mass% of the plating layer is high, it becomes difficult to form the ZnO layer on the entire surface, and the Fe-Zn
The alloy layer is oxidized and scales are easily generated. In addition, when the coating amount is small, the ZnO layer is not formed sufficiently, so the scale generation is not suppressed, and when the coating amount is large, the ZnO layer is sufficiently formed, but the interdiffusion of Fe and Zn However, the molten zinc layer remains and the mold is contaminated during pressing.
【００１４】以上より、予め、めっき層の初期Fe質量％
およびめっき付着量を適正化することで、スケールの生
成を抑制しつつ熱間プレスを行うことができる。なお、
このZnO 層は薄く、剥離して害を与えることはない。ま
た、塗装密着性を阻害することもないことは確認してい
る。From the above, the initial Fe mass% of the plating layer was previously determined.
Also, by optimizing the amount of deposit on the plating, hot pressing can be performed while suppressing generation of scale. In addition,
This ZnO layer is thin and does not peel off and cause harm. It has also been confirmed that it does not hinder the coating adhesion.
【００１５】以上ような知見に基づき完成させた本発明
は、次の通りである。
(1) 質量％で、Ｃ：0.08〜0.45％、Mnおよび／またはCr
合計で0.5 〜3.0 ％を含有する鋼板に、Fe含有量が５〜
80質量％であるFe−Zn合金から成りかつZn付着量が10〜
90g/m2であるZnめっき層を有することを特徴とする熱間
プレス用鋼板。The present invention completed based on the above findings is as follows. (1)% by mass, C: 0.08 to 0.45%, Mn and / or Cr
Fe content of 5-3.0% in steel plate containing 0.5-3.0% in total
It consists of Fe-Zn alloy with 80 mass% and the Zn deposition amount is 10 ~
A steel sheet for hot pressing, which has a Zn plating layer of 90 g / m 2 .
【００１６】(2) 前記鋼板が、さらに、質量％で、Si：
0.5 ％以下、Ｐ：0.05％以下、Ｓ：0.05％以下、Ni：２
％以下、Cu：１％以下、Mo：１％以下、Ｖ：１％以下、
Ti：１％以下、Nb：１％以下、Al：１％以下、および
Ｎ：0.01％以下から成る群から選んだ１種または２種以
上を含有することを特徴とする上記(1) に記載の熱間プ
レス用鋼板。(2) The steel sheet may further contain Si:
0.5% or less, P: 0.05% or less, S: 0.05% or less, Ni: 2
% Or less, Cu: 1% or less, Mo: 1% or less, V: 1% or less,
Ti: 1% or less, Nb: 1% or less, Al: 1% or less, and N: 0.01% or less, and one or more kinds selected from the group are contained, and the above (1) is included. Steel plate for hot pressing.
【００１７】(3) 前記鋼板が、さらに、質量％で、Ｂ：
0.0001〜0.004 ％を含有することを特徴とする上記(1)
または（2)に記載の熱間プレス用鋼板。
(4) 例えば常法により熱間圧延、またはさらに冷間圧延
を行って得た鋼板に、連続溶融亜鉛めっきラインにて、
溶融亜鉛めっきと合金化処理を行う製造方法において、
連続溶融亜鉛めっきラインでの最高加熱温度鈍がAc1 点
未満であり、合金化処理温度が500 ℃以上、Ac1 点以下
であることを特徴とする上記(1) 〜(3)のいずれかに記
載の熱間プレス用鋼板の製造方法。(3) The steel sheet further contains B:
Above (1) characterized by containing 0.0001 to 0.004%
Alternatively, the steel sheet for hot pressing according to (2). (4) For example, in a continuous hot-dip galvanizing line, to a steel sheet obtained by hot rolling by a conventional method, or further cold rolling.
In a manufacturing method of performing hot dip galvanizing and alloying treatment,
One of the above (1) to (3), wherein the maximum heating temperature blunt in the continuous hot dip galvanizing line is less than Ac 1 point and the alloying temperature is 500 ° C or higher and Ac 1 point or lower. The method for producing a steel sheet for hot pressing according to.
【００１８】(5) 鋼板に、連続溶融亜鉛めっきラインに
て、溶融亜鉛めっきと合金化処理を行う溶融亜鉛めっき
鋼板の製造方法において、連続溶融亜鉛めっきラインで
の最高加熱温度がAc1 点以上のとき、当該最高加熱温度
から500 ℃までの平均冷却速度を鋼の臨界冷却速度未満
とし、合金化処理温度が500 ℃以上、Ac1 点、以下であ
ることを特徴とする請求項１〜３のいずれかに記載の熱
間プレス用鋼板の製造方法。(5) In the method for producing a hot-dip galvanized steel sheet in which hot-dip galvanizing and alloying treatment is performed on a steel sheet in a continuous hot-dip galvanizing line, the maximum heating temperature in the continuous hot-dip galvanizing line is Ac 1 point or more. At that time, the average cooling rate from the maximum heating temperature to 500 ° C is set to be less than the critical cooling rate of steel, and the alloying treatment temperature is 500 ° C or more and Ac 1 point or less. A method for manufacturing a steel sheet for hot pressing according to any one of 1.
【００１９】[0019]
【発明の実施の形態】次に、本発明において、鋼組成、
めっき組成および製造時の加熱条件を各範囲に限定した
理由について説明する。本明細書において合金元素につ
いての「％」は「質量％」を表す。BEST MODE FOR CARRYING OUT THE INVENTION Next, in the present invention, a steel composition,
The reason for limiting the plating composition and the heating conditions at the time of manufacturing to each range will be described. In the present specification, “%” for alloy elements represents “mass%”.
【００２０】1. 素地鋼板成分について
鋼板の化学組成については、以下のように規定する。
Ｃ：0.08〜0.45％
Ｃは、鋼板の焼入れ性を高めかつ熱間プレス後強度を決
定する重要な元素である。しかしＣ含有量が0.08％未満
では、その効果は十分ではなく、一方でＣ含有量が0.45
％を超えると靭性劣化や溶接性劣化を招く。より望まし
いＣ含有量は0.1 〜0.3 ％である。1. Concerning base steel plate composition The chemical composition of the steel plate is defined as follows. C: 0.08 to 0.45% C is an important element that enhances the hardenability of the steel sheet and determines the strength after hot pressing. However, if the C content is less than 0.08%, the effect is not sufficient, while the C content is 0.45%.
%, Deterioration of toughness and weldability will be caused. A more desirable C content is 0.1 to 0.3%.
【００２１】Mnおよび／またはCr (合計) ：0.5 〜3.0
％
MnおよびCrは、鋼板の焼入れ性を高めかつ熱間プレス後
の強度を安定して確保するために、非常に効果のある元
素である。しかし（Mnおよび／またはCr）の合計含有量
が0.5 ％未満ではその効果は十分ではなく、一方で（Mn
および／またはCr）合計含有量が3.0 ％を超えるとその
効果は飽和し、逆に安定した強度確保が困難となる。よ
り望ましい（Mnおよび／またはCr) の合計含有量は0.8
〜2.0 ％である。Mn and / or Cr (total): 0.5 to 3.0
% Mn and Cr are very effective elements for enhancing the hardenability of the steel sheet and stably securing the strength after hot pressing. However, if the total content of (Mn and / or Cr) is less than 0.5%, the effect is not sufficient, while (Mn and / or Cr)
When the total content of Cr and / or Cr) exceeds 3.0%, the effect is saturated, and on the contrary, it becomes difficult to secure stable strength. More desirable (Mn and / or Cr) total content is 0.8
~ 2.0%.
【００２２】本発明によれば、熱間プレスによる焼入れ
性を確保することができればよく、そのためには、上述
のように、Ｃ、MnおよびCrの含有量が規定されるだけで
十分である。According to the present invention, it is sufficient to ensure the hardenability by hot pressing, and for that purpose, it is sufficient to specify the contents of C, Mn and Cr as described above.
【００２３】本発明の好適態様にあっては、さらに強度
を高めるために、あるいは、それらを一層安定して実現
するために、次のようにその添加元素を規定する。
Si：0.5 ％以下、Ｐ：0.05％以下、Ｓ：0.05％以下、N
i：２％以下、Cu：１％以下、Mo：１％以下、Ｖ：１％
以下、Ti：１％以下、Nb：１％以下、Al：１％以下、
Ｎ：0.01％以下
これらの元素も、鋼板の焼入れ性を高めかつ熱間プレス
後強度の安定確保に効果の有る元素である。しかし、上
限値を超えて含有させてもその効果は小さく、かついた
ずらにコスト増を招くため、各合金元素の含有量は上述
の範囲とする。In a preferred embodiment of the present invention, in order to further increase the strength or to realize them in a more stable manner, the additive element is defined as follows. Si: 0.5% or less, P: 0.05% or less, S: 0.05% or less, N
i: 2% or less, Cu: 1% or less, Mo: 1% or less, V: 1%
Below, Ti: 1% or less, Nb: 1% or less, Al: 1% or less,
N: 0.01% or less These elements are also effective in enhancing the hardenability of the steel sheet and ensuring stable strength after hot pressing. However, even if the content exceeds the upper limit, the effect is small and the cost is unnecessarily increased, so the content of each alloying element is set within the above range.
【００２４】ただし、Ｐ、Ｓについては不可避的に存在
することがあり、またSiおよび／またはAlについては脱
酸材として添加されることもある。Ｂ：0.0001〜0.004
％
Ｂは、鋼板の焼入れ性を高め、かつ熱間プレス後強度の
安定確保効果をさらに高める重要な元素である。しか
し、Ｂ含有量が0.0001％未満ではその効果は十分ではな
く、一方でＢ含有量が0.004 ％を超えるとその効果は飽
和し、かつコスト増を招く。より望ましいＢ含有量は0.
0005〜0.002 ％である。However, P and S may exist inevitably, and Si and / or Al may be added as a deoxidizing material. B: 0.0001 to 0.004
% B is an important element that enhances the hardenability of the steel sheet and further enhances the effect of stably securing the strength after hot pressing. However, if the B content is less than 0.0001%, the effect is not sufficient, while if the B content exceeds 0.004%, the effect is saturated and the cost increases. A more desirable B content is 0.
It is 0005 to 0.002%.
【００２５】2. Fe−Zn合金層（めっき層）について
Fe質量％：５〜80％
めっき層中の初期Fe含有量を適正化することで、大気中
で加熱しても熱間プレスに有害なスケール生成を前述の
ように抑制することができる。めっき層の初期Fe質量％
が低くて融点が低い場合には、FeとZnの相互拡散が十分
進まずZnの蒸気圧が高くなるためZnO 層が全面に形成さ
れる前にZnが蒸発し、スケール生成が抑制できない。一
方、めっき層の初期Fe質量％が高い場合には、ZnO 層が
全面に形成されづらくなり、下層のFe-Zn 合金層が酸化
され、スケールが生成しやすくなる。望ましい範囲は10
〜30％である。さらに望ましい範囲は13〜20％である。2. Fe-Zn alloy layer (plating layer) Fe mass%: 5 to 80% By optimizing the initial Fe content in the plating layer, it is harmful to hot pressing even when heated in the atmosphere. It is possible to suppress the generation of various scales as described above. Initial Fe mass% of plating layer
In the case of a low melting point and a low melting point, the mutual diffusion of Fe and Zn does not proceed sufficiently and the vapor pressure of Zn becomes high, so that Zn evaporates before the ZnO layer is formed on the entire surface, and scale formation cannot be suppressed. On the other hand, when the initial Fe mass% of the plating layer is high, it becomes difficult to form the ZnO layer on the entire surface, the Fe-Zn alloy layer as the lower layer is oxidized, and scale is easily generated. The preferred range is 10
~ 30%. A more desirable range is 13 to 20%.
【００２６】ここに、「初期」というのは、加熱による
ZnO 生成に先立ってという意味であり、具体的には、熱
間プレスに際して行われる加熱に先立ってという趣旨で
ある。"Initial" here is due to heating.
This means prior to the production of ZnO, and specifically, prior to the heating performed during hot pressing.
【００２７】なお、めっき層のFeおよびZn以外の組成に
は特に制限はなく、Al、Mn、Ni、Cr、Co、Mg、Sn、Pbな
どの合金元素をその目的に応じて適宜量添加しためっき
層であってもよい。その他原料等から不可避的に混入す
ることがあるBe、Ｂ、Si、Ｐ、Ｓ、Ti、Ｖ、Ｗ、Mo、S
b、Cd、Nb、Cu、Sr等のうちのいくつかが含有されるこ
ともある。The composition of the plating layer other than Fe and Zn is not particularly limited, and alloying elements such as Al, Mn, Ni, Cr, Co, Mg, Sn, and Pb are added in appropriate amounts according to the purpose. It may be a plating layer. Be, B, Si, P, S, Ti, V, W, Mo, S that may be inevitably mixed from other raw materials
Some of b, Cd, Nb, Cu, Sr, etc. may be contained.
【００２８】かかるめっき層は通常鋼板表面に直接設け
られているが、かかるめっき層と鋼板表面との間に他の
めっき層等が介在していてもよい。まためっき層は通常
両面に設けられるが、他の面が熱間プレスに有害でない
予備処理層、あるいは保護層を有している限り、片面だ
けに本発明にかかる上述のめっき層を設けてもよい。め
っき付着量について
めっき付着量：Zn重量に換算し、鋼板片面あたり10〜90
g/m2
めっき付着量を適正化することで、大気中で加熱しても
熱間プレスに有害なスケール生成を前述のように抑制す
ることができる。めっき付着量が少ない場合には、ZnO
層が十分に形成されないためスケール発生が抑制され
ず、めっき付着量が多い場合には、ZnO 層は十分に形成
されるが、FeとZnの相互拡散が十分進まず溶融亜鉛層が
残存するため、プレス時に溶融亜鉛層が飛散して金型が
汚染される。より望ましい範囲は20〜80g/m2である。The plating layer is usually provided directly on the surface of the steel sheet, but another plating layer or the like may be interposed between the plating layer and the surface of the steel sheet. The plating layer is usually provided on both surfaces, but as long as the other surface has a pretreatment layer or a protective layer that is not harmful to hot pressing, the above-mentioned plating layer according to the present invention may be provided on only one surface. Good. Coating weight: Plating weight: Converted to Zn weight, 10 to 90 per side of steel plate
By optimizing the coating amount of g / m 2 plating, it is possible to suppress scale generation, which is harmful to hot pressing, even if it is heated in the atmosphere, as described above. ZnO is used when the coating amount is small
The scale is not suppressed because the layer is not formed sufficiently, and when the amount of plating is large, the ZnO layer is formed sufficiently, but the mutual diffusion of Fe and Zn does not proceed sufficiently and the molten zinc layer remains. , The molten zinc layer is scattered during pressing and the mold is contaminated. A more desirable range is 20 to 80 g / m 2 .
【００２９】3. 製造方法について
本発明にかかる鋼板は、熱間プレスの際にオーステナイ
ト域またはオーステナイト域近傍に加熱され、その温度
域でプレス成形される。したがって、加熱前の室温での
機械的性質は重要ではなく、加熱前の金属組織について
は特に規定しない。つまり、めっき前の素地鋼板として
熱延鋼板または冷延鋼板のいずれを使用してもよく、い
わゆる鋼板であればよく、その製造方法については限定
しない。しかし、生産性の観点から、好適な製造方法を
以下に述べる。3. Manufacturing Method The steel sheet according to the present invention is heated in the austenite region or in the vicinity of the austenite region during hot pressing, and is press-formed in that temperature region. Therefore, the mechanical properties at room temperature before heating are not important, and the metallographic structure before heating is not particularly specified. That is, either a hot-rolled steel sheet or a cold-rolled steel sheet may be used as the base steel sheet before plating, as long as it is a so-called steel sheet, and its manufacturing method is not limited. However, from the viewpoint of productivity, a suitable manufacturing method will be described below.
【００３０】熱間圧延：熱間圧延は、常法により行えば
よく、圧延の安定性の観点から、オーステナイト域で行
うことが好ましい。巻取温度が低いと、マルテンサイト
組織となって強度が上昇し、連続溶融亜鉛めっきライン
の通板や、冷間圧延が困難になる。一方、巻取温度が高
いと、酸化スケールが厚くなり、引き続き行う酸洗の効
率が低下したり、また、酸洗を行わず直接めっきする場
合は、めっき密着性が劣化する。したがって、巻取温度
は、500 〜600 ℃が好ましい。Hot rolling: Hot rolling may be carried out by a conventional method, and from the viewpoint of rolling stability, it is preferably carried out in the austenite region. When the coiling temperature is low, a martensite structure is formed and the strength is increased, which makes it difficult to pass a continuous hot-dip galvanizing line and to perform cold rolling. On the other hand, when the coiling temperature is high, the oxide scale becomes thick and the efficiency of the subsequent pickling decreases, and the plating adhesion deteriorates when direct plating is performed without pickling. Therefore, the winding temperature is preferably 500 to 600 ° C.
【００３１】冷間圧延：冷間圧延は、常法によっておこ
なう。本発明の鋼板は炭素量が多いため、過度の圧下率
で冷間圧延するとミルの負担が大きくなる。また、加工
硬化により冷間圧延後の強度が高くなりすぎると、亜鉛
めっきラインにて、コイル接続時の溶接強度やライン通
板能力が問題となる。したがって、圧下率は80％以下が
好ましく、70％以下がさらに好ましい。Cold rolling: Cold rolling is performed by a conventional method. Since the steel sheet of the present invention has a large amount of carbon, if the steel sheet is cold-rolled at an excessive reduction rate, the load on the mill will increase. Further, if the strength after cold rolling becomes too high due to work hardening, the welding strength and the line threading ability at the time of coil connection become a problem in the galvanizing line. Therefore, the rolling reduction is preferably 80% or less, more preferably 70% or less.
【００３２】なお、冷間圧延を行うとそれだけコスト増
となるので、熱間圧延で製造可能な板厚、板幅の鋼板に
ついては、冷間圧延を省略し、熱間圧延ままの鋼板を用
いるのが好ましい。Since cold rolling increases the cost accordingly, cold rolling is omitted for a steel plate having a plate thickness and a plate width which can be manufactured by hot rolling, and a steel plate as hot rolled is used. Is preferred.
【００３３】亜鉛めっき：本発明にかかるめっき鋼板の
めっき層の形成は、溶融亜鉛めっき、電気めっき、溶
射、蒸着等、その方法は限定されない。また、鋼帯を連
続処理してもよいし、切り板単体で処理してもよい。一
般には、生産効率に優れた連続溶融亜鉛めっきラインを
用いるのが好ましい。したがって、以下に連続溶融亜鉛
めっき方法について説明する。Galvanization: The method of forming the plating layer of the plated steel sheet according to the present invention is not limited to hot-dip galvanizing, electroplating, thermal spraying, vapor deposition or the like. Further, the steel strip may be continuously treated, or may be treated as a single cut plate. Generally, it is preferable to use a continuous hot-dip galvanizing line which is excellent in production efficiency. Therefore, the continuous hot dip galvanizing method will be described below.
【００３４】通常の連続溶融亜鉛めっきラインは、加熱
炉、冷却ゾーン、溶融亜鉛浴、合金化炉が連続して配置
されている。本発明においては、素地鋼板の金属組織を
特に限定しないので、加熱炉および冷却ゾーンにおける
ヒートパタンは特に限定されない。しかしながら、本発
明にかかる鋼板は炭素量が高く、焼きが入り易い成分で
あるため、ライン中で非常に高強度の鋼板になる恐れが
ある。通板の容易性、製造可能範囲（板厚、板幅）を考
慮して、鋼板が過度に高強度にならないヒートパタンが
好ましい。In a normal continuous hot-dip galvanizing line, a heating furnace, a cooling zone, a hot-dip zinc bath, and an alloying furnace are continuously arranged. In the present invention, since the metal structure of the base steel sheet is not particularly limited, the heat pattern in the heating furnace and the cooling zone is not particularly limited. However, since the steel sheet according to the present invention has a high carbon content and is a component that is easily tempered, it may become a steel sheet with extremely high strength in the line. Considering the ease of passing the plate and the manufacturable range (plate thickness, plate width), a heat pattern that does not cause the steel plate to have excessively high strength is preferable.
【００３５】最大加熱温度：溶融めっきに先立って行う
加熱に際して、加熱炉における加熱温度がAc1 点未満の
場合、加熱中に鋼板の回復、再結晶が起こり、加熱前と
比較し強度は低下する。したがって、通板性に問題を生
じることはない。炉の加熱エネルギーを節約する観点か
らは、めっき性を阻害しない範囲で、低温で加熱するこ
とが好ましい。Maximum heating temperature: When heating is performed prior to hot dip coating, if the heating temperature in the heating furnace is less than Ac 1 point, recovery and recrystallization of the steel sheet will occur during heating and the strength will decrease compared to before heating. . Therefore, there is no problem in sheet passing property. From the viewpoint of saving the heating energy of the furnace, it is preferable to heat at a low temperature as long as the plating property is not impaired.
【００３６】一方、最大加熱温度がAc1 点以上の場合、
加熱中に鋼板の回復、再結晶が起きるとともに、オース
テナイト相が出現し、その後の冷却条件によっては、高
強度の変態生成相が形成される。On the other hand, when the maximum heating temperature is Ac 1 point or higher,
While the steel sheet recovers and recrystallizes during heating, an austenite phase appears, and depending on the subsequent cooling conditions, a high-strength transformation-forming phase is formed.
【００３７】冷却速度：溶融めっき浴は通常460 ℃程度
に保持されており、加熱された鋼板はめっき浴温度にま
で冷却される。このとき加熱温度がAc1 点未満の場合、
冷却速度は金属組織に影響しないので、任意の速度で冷
却して良い。Cooling rate: The hot dip plating bath is usually maintained at about 460 ° C., and the heated steel sheet is cooled to the plating bath temperature. At this time, if the heating temperature is less than Ac 1 point,
Since the cooling rate does not affect the metal structure, it may be cooled at any rate.
【００３８】Ac1 点以上に加熱してオーステナイトが生
じた場合、冷却速度が速すぎると、オーステナイトがベ
イナイトまたはマルテンサイト主体の組織に変態し、鋼
板の強度が高くなるので好ましくない。具体的には、最
高加熱温度から、500 ℃までの平均冷却速度を、臨界冷
却速度以下にすることが好ましい。When austenite is generated by heating to the Ac 1 point or more, if the cooling rate is too fast, the austenite transforms into a structure mainly composed of bainite or martensite, and the strength of the steel sheet increases, which is not preferable. Specifically, it is preferable that the average cooling rate from the maximum heating temperature to 500 ° C. be equal to or lower than the critical cooling rate.
【００３９】なお、この臨界冷却速度の測定方法は、後
述する実施例にてさらに具体的に説明する。臨界冷却速
度は、鋼板の焼入性の指標として用いるものであり、マ
ルテンサイト単相組織を生じる冷却速度である。上述の
条件で冷却された鋼板に少量のベイナイトまたはマルテ
ンサイトが含まれていたとしても、本発明の製造方法の
効果が否定されるものではない。しかしながら、できる
だけ低強度にして通板性を高めるという観点からは、冷
却速度をできるだけ遅くし、マルテンサイトを形成しな
いことが好ましい。The method of measuring the critical cooling rate will be described more specifically in the examples described later. The critical cooling rate is used as an index of hardenability of a steel sheet, and is a cooling rate that produces a martensite single phase structure. Even if the steel sheet cooled under the above conditions contains a small amount of bainite or martensite, the effect of the production method of the present invention cannot be denied. However, from the viewpoint of making the strength as low as possible to enhance the sheet passing property, it is preferable to make the cooling rate as slow as possible and not form martensite.
【００４０】溶融亜鉛めっき：常法により、溶融した亜
鉛および亜鉛合金めっき浴に鋼板を浸漬して引き上げれ
ばよい。めっき付着量の制御は引き上げ速度やノズルよ
り吹き出すワイビングガスの流量調整により行われる。Hot dip galvanizing: The steel plate may be immersed in a molten zinc and zinc alloy plating bath and pulled up by a conventional method. The amount of plating adhered is controlled by adjusting the pulling rate and the flow rate of the wiping gas blown from the nozzle.
【００４１】合金化処理温度：溶融亜鉛めっき処理を行
ったのち、ガス炉、誘導加熱炉等で再加熱することによ
り行われ、めっき層と素地鋼板との間で金属拡散が行わ
れ合金化が進行する。Alloying treatment temperature: It is carried out by performing hot dip galvanizing treatment and then reheating it in a gas furnace, an induction heating furnace, etc., and metal diffusion is carried out between the plating layer and the base steel sheet for alloying. proceed.
【００４２】本発明によりめっき層中の初期Fe質量％を
５〜80％に高めるためには、500 ℃以上で合金化するこ
とが望ましい。合金化温度が500 ℃未満では合金化速度
が遅いため、ライン速度を低下させる必要が生じて生産
性を阻害したり、合金化炉を長くする等の設備的対応が
必要となる。合金化温度が高いほど、合金化速度が速く
なるが、Ac1 点以上の合金化温度では、上述した最大加
熱温度の場合と同じ理由により鋼板が高強度化してしま
う。好ましい範囲は、550 〜650 ℃である。In order to increase the initial Fe mass% in the plating layer to 5 to 80% according to the present invention, it is desirable to alloy at 500 ° C. or higher. If the alloying temperature is less than 500 ° C, the alloying speed is slow, so it is necessary to reduce the line speed, which hinders productivity and requires a facility measure such as lengthening the alloying furnace. The higher the alloying temperature is, the faster the alloying rate is. However, at the alloying temperature of Ac 1 point or higher, the steel sheet becomes high in strength for the same reason as in the case of the maximum heating temperature described above. The preferred range is 550-650 ° C.
【００４３】後処理：Feめっき等の後処理は、必要に応
じて適宜行えばよい。後処理としてめっきを行ったとき
は溶融めっき層との合計で、本発明で規定する条件を満
たせばよい。通常、後処理でのめっき付着量は少量であ
るので、本発明の本質に影響しない。Post-treatment: Post-treatment such as Fe plating may be appropriately performed as necessary. When plating is performed as a post-treatment, the total of the amount of the hot-dip layer and the hot-dip layer should satisfy the conditions specified in the present invention. Usually, since the amount of plating applied in the post-treatment is small, it does not affect the essence of the present invention.
【００４４】調質圧延：鋼板の平坦矯正、表面粗度の調
整のために、調質圧延を行ってもよい。
4．熱間プレスについて
本発明にかかる鋼板の熱間プレス成形は特に制限はな
く、通常行われているプレス成形を熱間にて行えばよ
い。すなわち、Ac3 点以上に加熱した鋼板を、臨界冷却
速度以上で冷却できる方法で成形すれば、母材成分で決
定される最高強度が得られる。Temper rolling: Temper rolling may be performed in order to straighten the steel sheet and adjust the surface roughness. Four. Hot Pressing There is no particular limitation on the hot press forming of the steel sheet according to the present invention, and the press forming that is normally performed may be performed hot. That is, if a steel sheet heated to the Ac 3 point or higher is formed by a method capable of cooling at a critical cooling rate or higher, the maximum strength determined by the base metal components can be obtained.
【００４５】[0045]
【実施例】(実施例１)表１に示した組成の鋼を実験室で
溶製し、スラブとなした。このスラブを1200℃にて30分
加熱した後、900 ℃以上で熱間圧延を行い、板厚3.2mm
の鋼板とした。熱間圧延後は、550 ℃まで水スプレー冷
却したのち炉に装入し、550 ℃で30分保持した後、20℃
／時で室温まで徐冷することにより、熱間圧延後の巻き
取り工程をシミュレ一トした。熱延板は、酸洗によりス
ケールを除去した後、冷間圧延にて板厚1.0mm とした。
この素地鋼板の切板に、めっきシミュレ一タを用いて溶
融亜鉛めっきを施し、その後、合金化処理を行った。ま
ためっき層のFe含有量を変化させているが、これは合金
化処理温度(500〜800 ℃）や時間（30分以下）を変化さ
せることにより行った。Example 1 A steel having the composition shown in Table 1 was melted in a laboratory to form a slab. After heating this slab at 1200 ° C for 30 minutes, hot rolling it at 900 ° C or more to obtain a plate thickness of 3.2 mm.
Steel plate. After hot rolling, cool by water spray to 550 ° C, put in the furnace, hold at 550 ° C for 30 minutes, then 20 ° C.
The winding process after hot rolling was simulated by gradually cooling to room temperature at 1 / hour. The hot rolled sheet was pickled to remove the scale and then cold rolled to a sheet thickness of 1.0 mm.
Hot-dip galvanizing was applied to the cut plate of this base steel sheet using a plating simulator, and then alloying treatment was performed. The Fe content of the plating layer was changed by changing the alloying treatment temperature (500 to 800 ° C) and time (30 minutes or less).
【００４６】幅50mmの短冊に切断した鋼板を大気雰囲気
の加熱炉内で850 ℃×３分加熱して、加熱炉より取り出
し、このままの高温状態でハット形状に熱間プレス成形
を行った。このときの金型は、パンチ幅50mm、パンチ肩
R5mm、ダイ肩R5mm、成形深さ25mmで実施した。またプレ
ス後のハット立壁部中央について、ビッカース硬度測定
（荷重9.8N、測定数：10）も行った。なお、本実施例に
おいては、鋼板の温度ははぼ２分で850 ℃に到達してい
た。A steel sheet cut into a strip of 50 mm in width was heated in an air atmosphere heating furnace at 850 ° C. for 3 minutes, taken out from the heating furnace, and hot press-formed into a hat shape in the same high temperature state. The die at this time has a punch width of 50 mm and a punch shoulder.
R5mm, die shoulder R5mm, molding depth 25mm. Vickers hardness measurement (load: 9.8 N, number of measurements: 10) was also performed on the center of the standing wall of the hat after pressing. In this example, the temperature of the steel sheet reached 850 ° C in 2 minutes.
【００４７】このようにして得られた熱間プレス成形品
について、下記要領で、成形後の外観、塗膜密着性、塗
装後耐食性（以後、耐食性と呼称する）をぞれぞれ評価
した。The hot press-molded products thus obtained were evaluated for appearance after molding, adhesion of coating film, and corrosion resistance after coating (hereinafter referred to as corrosion resistance) in the following manner.
【００４８】(1) 成形後の外観
鉄系酸化物からなる有害なスケール形成の有無を評価
し、スケールが形成された場合には×、形成されなかっ
た場合には○とした。またプレス金型への残存溶融亜鉛
層の飛散による汚染有無を評価し、金型汚染が無かった
場合には○、金型汚染があった場合には×とした。(1) Appearance after molding The presence or absence of harmful scale formation of an iron-based oxide was evaluated. When scale was formed, it was rated as x, and when it was not, it was rated as o. In addition, the presence or absence of contamination due to the scattering of the residual molten zinc layer on the press die was evaluated. When there was no die contamination, it was rated as O, and when there was die contamination, it was rated as X.
【００４９】(2) 塗膜密着性試験
本例で得た片ハット成形品から切り出した試験片に、日
本パーカライジング（株）製PBL-3080で通常の化成処理
条件により燐酸亜鉛処理したのち関西ペイント製電着塗
料GT-lO を電圧200Vのスロープ通電で電着塗装し、焼き
付け温度150 ℃で20分焼き付け塗装した。塗膜厚みは20
μm であった。試験片を50℃のイオン交換水に浸潰し24
0 時間後に取り出して、カッターナイフで１mm幅の碁盤
目状に傷を入れ、ニチバン製のポリエステルテープで剥
離テストを行い、塗膜の残存マス数を比較し、塗膜密着
性を評価した。なお、全マス数は100 個とした。評価基
準は残存マス数90〜100 個を良好：評価記号○、０〜89
個を不良：評価記号×とした。(2) Coating Film Adhesion Test The test piece cut out from the one-hat molded article obtained in this example was treated with zinc phosphate under normal chemical conversion treatment conditions using PBL-3080 manufactured by Nippon Parkerizing Co., Ltd., and then Kansai Paint. The electrodeposition paint GT-lO was electrodeposited by applying a voltage of 200 V with slope energization, and baked at a baking temperature of 150 ° C for 20 minutes. Coating thickness is 20
It was μm. Immerse the test piece in 50 ° C ion-exchanged water 24
After 0 hours, it was taken out, scratches were made in a grid pattern of 1 mm width with a cutter knife, a peeling test was conducted with a polyester tape made by Nichiban, and the number of remaining masses of the coating film was compared to evaluate the coating film adhesion. The total number of cells was 100. The evaluation standard is 90 to 100 remaining masses are good: evaluation symbol ○, 0 to 89
Bad pieces: evaluated with an evaluation symbol x.
【００５０】(3) 塗装後耐食性試験 (耐食性試験)
塗膜密着性試験と同様の方法で塗装した後、試験片の塗
膜にカッターナイフで素地に達するスクラッチ傷を入
れ、JIS Z2371 に規定された塩水噴霧試験を480時間行
った。傷部からの塗膜膨れ幅もしくは錆幅を測定し、塗
装後耐食性を評価した。評価基準は錆幅、塗膜膨れ幅の
いずれか大きい方の値で０mm以上〜４mm未満を良好：評
価記号○、４mm以上を不良：評価記号×とした。(3) Corrosion resistance test after coating (corrosion resistance test) After coating by the same method as the coating adhesion test, the coating of the test piece was scratched with a cutter knife to reach the base, and was specified in JIS Z2371. The salt spray test was performed for 480 hours. The coating swelling width or rust width from the scratched portion was measured to evaluate the corrosion resistance after coating. The evaluation criterion is 0 mm or more and less than 4 mm, whichever is larger depending on which of the rust width and the swelling width of the coating film, is evaluated as good: evaluation symbol ◯, and 4 mm or more is defective: evaluation symbol x.
【００５１】以上の結果をまとめて表１に示す。The above results are summarized in Table 1.
【００５２】[0052]
【表１】 [Table 1]
【００５３】本発明例である鋼種No.1〜10では、鉄系酸
化物の形成状況、金型汚染、塗膜密着性および耐食性と
もに良好な結果であった。一方、比較例である鋼種No.1
1 〜15では、鉄系酸化物の形成状況、金型汚染、塗膜密
着性および耐食性を同時に満足できるものはなかった。In the steel types Nos. 1 to 10 as the examples of the present invention, the results of forming iron oxides, mold contamination, coating adhesion and corrosion resistance were good. On the other hand, steel type No. 1 which is a comparative example
In Nos. 1 to 15, none of the iron-based oxide formation conditions, mold contamination, coating adhesion and corrosion resistance were simultaneously satisfied.
【００５４】(実施例２）表１の鋼種No.6に示した組成
の鋼を実験室で溶製し、スラブとした。このスラブを12
00℃にて30分加熱した後、900 ℃以上で熱間圧延を行
い、板厚3.2mm の鋼板とした。熱間圧延後は、550 ℃ま
で水スプレー冷却したのち炉に装入し、550℃で30分保
持した後、20℃/ 時で室温まで徐冷することにより、熱
間圧延後の巻き取り工程をシミュレートした。熱延板
は、酸洗によりスケールを除去した後、冷間圧延にて板
厚1.0mm とした。この鋼板に、焼鈍シミュレーターを用
いて、溶融亜鉛めっきラインを模擬した熱履歴を与え
た。具体的な熱履歴は，図１および表２に示す。熱処理
後の鋼板の断面ビッカース硬度（荷重49Ｎ、測定数：
５）を測定した結果も、表２に併せて示す。Example 2 A steel having the composition shown in the steel type No. 6 in Table 1 was melted in a laboratory to form a slab. This slab 12
After heating at 00 ° C for 30 minutes, hot rolling was performed at 900 ° C or higher to obtain a steel plate with a thickness of 3.2 mm. After hot rolling, after water spray cooling to 550 ° C, put in the furnace, hold at 550 ° C for 30 minutes, and then gradually cool to room temperature at 20 ° C / hour to wind up after hot rolling. Was simulated. The hot rolled sheet was pickled to remove the scale and then cold rolled to a sheet thickness of 1.0 mm. An annealing simulator was used to give the steel sheet a thermal history simulating a hot dip galvanizing line. The specific thermal history is shown in FIG. 1 and Table 2. Cross-section Vickers hardness of steel sheet after heat treatment (load 49N, number of measurements:
The results of measuring 5) are also shown in Table 2.
【００５５】また、この鋼の焼き入れ性の指標として、
臨界冷却速度を測定した。熱延板から直径3.0mm 、長さ
10mmの円柱試験片を切り出し、大気中で950 ℃まで100
℃/分の昇温速度にて加熱し、その温度で５分間保持し
たのち、種々の冷却速度で室温まで冷却した。その後、
得られた試験片のビッカース硬度測定（荷重49Ｎ、測定
数：５）および組織観察を行った。また、加熱、冷却中
の試験片の熱膨張変化を測定することにより、Ac1 点お
よびAc3 点を測定した。As an index of the hardenability of this steel,
The critical cooling rate was measured. Diameter 3.0 mm from hot rolled plate, length
A 10 mm cylindrical test piece is cut out, and 100 up to 950 ° C in the atmosphere.
After heating at a temperature rising rate of ° C / min and holding at that temperature for 5 minutes, it was cooled to room temperature at various cooling rates. afterwards,
Vickers hardness measurement (load 49 N, number of measurements: 5) and structure observation of the obtained test piece were performed. In addition, Ac 1 point and Ac 3 point were measured by measuring the thermal expansion change of the test piece during heating and cooling.
【００５６】950 ℃からの冷却速度が速いほど硬度は上
昇し、ある冷却速度 (臨界冷却速度) 以上ではほぼ一定
になった。また、臨界冷却速度以上ではほぼマルテンサ
イト単相組織を示した。表１の鋼種No.6の鋼成分の臨界
冷却速度は、17℃/sであった。Ac1 点、Ac3 点はそれぞ
れ、728 ℃、823 ℃であった。The hardness increased as the cooling rate from 950 ° C. increased, and became almost constant above a certain cooling rate (critical cooling rate). Moreover, above the critical cooling rate, almost a martensitic single-phase structure was exhibited. The critical cooling rate of the steel composition of steel type No. 6 in Table 1 was 17 ° C / s. Ac 1 point and Ac 3 point were 728 ° C and 823 ° C, respectively.
【００５７】次に、表２の結果をみると、最高加熱温度
がAc1 点未満、すなわち728 ℃未満の場合、温度の上昇
に伴って鋼板は回復、再結晶して硬度が低下している
（番号2-1 、2-2)。最大加熱温度からめっき浴までの冷
却速度の影響は小さい（番号2-9 、2-10）。一方、最高
加熱温度がAc1 点以上の場合、冷却速度が速いと硬度が
上昇している（番号2-3 〜2-8 、2-11〜16）。さらに、
合金化温度がAc1 点より高い場合は（番号2-18、2-2
0）、硬度が上昇している。本発明範囲の条件の場合
は、いずれも硬度(Hv)が200 以下であり、良好な通板性
が確保できる。Next, looking at the results in Table 2, when the maximum heating temperature is less than the Ac 1 point, that is, less than 728 ° C., the steel sheet recovers and recrystallizes with a decrease in hardness as the temperature rises. (Numbers 2-1, 2-2). The effect of the cooling rate from the maximum heating temperature to the plating bath is small (No. 2-9, 2-10). On the other hand, when the maximum heating temperature is Ac 1 point or higher, the hardness increases when the cooling rate is fast (Nos. 2-3 to 2-8 and 2-11 to 16). further,
If the alloying temperature is higher than Ac 1 point (number 2-18, 2-2
0), hardness is increasing. In the case of the conditions of the range of the present invention, the hardness (Hv) is 200 or less in all cases, and good stripability can be secured.
【００５８】[0058]
【表２】 [Table 2]
【００５９】[0059]
【発明の効果】以上説明してきたように、本発明によれ
ば、安価なめっき鋼板を用いて熱間プレスを行うこと
で、加熱炉の雰囲気制御設備が不要となるほか、、プレ
ス成形時の鉄系酸化物の剥離処理工程も不要となり生産
工程を簡素化できコスト削減を図ることができる。また
犠牲防食効果のある亜鉛めっき層を有するためプレス成
形製品の耐食性も向上する。As described above, according to the present invention, by performing hot pressing using an inexpensive plated steel sheet, the atmosphere control equipment of the heating furnace is not required, and at the time of press forming. The iron-based oxide peeling process is not required, and the production process can be simplified and the cost can be reduced. Further, since the galvanized layer has a sacrificial anticorrosion effect, the corrosion resistance of the press-formed product is also improved.
【図１】連続溶融亜鉛めっきラインを模擬する熱履歴の
模式図である。FIG. 1 is a schematic diagram of a heat history simulating a continuous hot-dip galvanizing line.
フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２３Ｃ 2/16 Ｃ２３Ｃ 2/16 2/28 2/28 (72)発明者 今井 和仁 大阪府大阪市中央区北浜４丁目５番33号 住友金属工業株式会社内 Ｆターム(参考） 4K027 AA02 AA05 AA22 AB02 AB04 AB28 AB43 AC73 AE02 AE12 AE18 AE22 4K037 EA01 EA02 EA05 EA06 EA11 EA13 EA15 EA16 EA17 EA18 EA19 EA20 EA23 EA25 EA27 EA31 EA32 EB06 EB07 EB08 FA02 FA03 FC04 FD06 FE01 FE02 FE06 FG00 GA05 HA02Continuation of front page (51) Int.Cl. 7 Identification code FI theme code (reference) C23C 2/16 C23C 2/16 2/28 2/28 (72) Inventor Kazuhito Imai 4-chome Kitahama, Chuo-ku, Osaka-shi, Osaka No. 5 No. 33 Sumitomo Metal Industries, Ltd. in the F-term (reference) 4K027 AA02 AA05 AA22 AB02 AB04 AB28 AB43 AC73 AE02 AE12 AE18 AE22 4K037 EA01 EA02 EA05 EA06 EA11 EA13 EA15 EA16 EA17 EA18 EA19 EA20 EA23 EA25 EA27 EA31 EA32 EB06 EB07 EB08 FA02 FA03 FC04 FD06 FE01 FE02 FE06 FG00 GA05 HA02
Claims (5)
／またはCr合計で0.5 〜3.0 ％を含有する鋼板に、Fe含
有量が５〜80質量％であるFe-Zn 合金から成りかつZn付
着量が10〜90g/m2であるZnめっき層を有することを特徴
とする熱間プレス用鋼板。1. A steel sheet containing C: 0.08 to 0.45% and Mn and / or Cr in a total amount of 0.5 to 3.0% by mass, and an Fe-Zn alloy having an Fe content of 5 to 80% by mass. A steel sheet for hot pressing, which has a Zn plating layer having a Zn adhesion amount of 10 to 90 g / m 2 .
5 ％以下、Ｐ：0.05％以下、Ｓ：0.05％以下、Ni：２％
以下、Cu：１％以下、Mo：１％以下、Ｖ：１％以下、T
i：１％以下、Nb：１％以下、Al：１％以下、および
Ｎ：0.01％以下から成る群から選んだ１種または２種以
上を含有することを特徴とする請求項１に記載の熱間プ
レス用鋼板。2. The steel sheet further comprises, in mass%, Si: 0.
5% or less, P: 0.05% or less, S: 0.05% or less, Ni: 2%
Below, Cu: 1% or less, Mo: 1% or less, V: 1% or less, T
i: 1% or less, Nb: 1% or less, Al: 1% or less, and N: 0.01% or less, and one or more kinds selected from the group are contained, The claim 1 characterized by the above-mentioned. Steel plate for hot pressing.
0001〜0.004 ％を含有することを特徴とする請求項１ま
たは２に記載の熱間プレス用鋼板。3. The steel sheet, further in mass%, B: 0.
The steel sheet for hot pressing according to claim 1 or 2, which contains 0001 to 0.004%.
て、溶融亜鉛めっきと合金化処理を行う溶融亜鉛めっき
鋼板の製造方法において、連続溶融亜鉛めっきラインで
の最高加熱温度がAc1 点未満であり、合金化処理温度が
500 ℃以上、Ac 1 点以下であることを特徴とする請求項
１〜３のいずれかに記載の熱間プレス用鋼板の製造方
法。4. A continuous hot-dip galvanizing line for steel sheets.
, Hot dip galvanizing and alloying treatment
In the steel sheet manufacturing method, in the continuous hot dip galvanizing line
The maximum heating temperature of1Below the point, the alloying temperature is
500 ℃ or more, Ac 1Claims that are less than or equal to the point
1. A method of manufacturing a steel sheet for hot pressing according to any one of 1 to 3.
Law.
て、溶融亜鉛めっきと合金化処理を行う溶融亜鉛めっき
鋼板の製造方法において、連続溶融亜鉛めっきラインで
の最高加熱温度がAc1 点以上のとき、当該最高加熱温度
から500 ℃までの平均冷却速度を鋼の臨界冷却速度未満
とし、合金化処理温度が500 ℃以上、Ac 1 点、以下であ
ることを特徴とする請求項１〜３のいずれかに記載の熱
間プレス用鋼板の製造方法。5. A steel sheet and a continuous hot-dip galvanizing line.
, Hot dip galvanizing and alloying treatment
In the steel sheet manufacturing method, in the continuous hot dip galvanizing line
The maximum heating temperature of1When the number of points is above the point, the maximum heating temperature
Average cooling rate from ℃ to 500 ℃ less than the critical cooling rate of steel
And the alloying temperature is 500 ℃ or more, Ac 1Points, below
Heat according to any one of claims 1 to 3, characterized in that
Method for manufacturing steel sheet for hot pressing.
Priority Applications (11)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001342151A JP3582512B2 (en) | 2001-11-07 | 2001-11-07 | Steel plate for hot pressing and method for producing the same |
| AT02777929T ATE468416T1 (en) | 2001-10-23 | 2002-10-23 | METHOD FOR HOT PRESSING A PLATED STEEL PRODUCT |
| PCT/JP2002/010972 WO2003035922A1 (en) | 2001-10-23 | 2002-10-23 | Method for press working, plated steel product for use therein and method for producing the steel product |
| EP02777929.7A EP1439240B2 (en) | 2001-10-23 | 2002-10-23 | Method for hot-press forming a plated steel product |
| CNB028210816A CN100434564C (en) | 2001-10-23 | 2002-10-23 | Hot press forming method, and a plated steel material therefor and its manufacturing method |
| CN200710137324XA CN101144162B (en) | 2001-10-23 | 2002-10-23 | Hot press forming method, electroplating steel products thereof and preparation method for the same |
| KR1020067014733A KR100678406B1 (en) | 2001-10-23 | 2002-10-23 | Hot press forming method for steel material |
| DE60236447T DE60236447D1 (en) | 2001-10-23 | 2002-10-23 | PROCESS FOR HOT PRESS PROCESSING OF A PLATED STEEL PRODUCT |
| KR1020047005977A KR100646619B1 (en) | 2001-10-23 | 2002-10-23 | Method for press working, plated steel product for use therein and method for producing the steel product |
| US10/730,978 US20040166360A1 (en) | 2001-10-23 | 2003-12-10 | Hot press forming method, and a plated steel material therefor and its manufacturing method |
| US11/186,973 US7673485B2 (en) | 2001-10-23 | 2005-07-22 | Hot press forming method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001342151A JP3582512B2 (en) | 2001-11-07 | 2001-11-07 | Steel plate for hot pressing and method for producing the same |
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| Publication Number | Publication Date |
|---|---|
| JP2003147499A true JP2003147499A (en) | 2003-05-21 |
| JP3582512B2 JP3582512B2 (en) | 2004-10-27 |
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ID=19156055
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| Country | Link |
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| JP (1) | JP3582512B2 (en) |
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2001
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