WO2025079386A1 - Hot-stamp molded body - Google Patents

Abstract

The present invention provides a hot-stamp molded body comprising a steel base material, and a plating layer disposed on the surface of the steel base material, the hot-stamp molded bod being characterized in that: the plating layer has a predetermined chemical composition; the plating layer includes, in order from the steel base material side, an Fe₂Al₅ phase, an Fe-Al phase having an Fe content of 20-40 mass%, and a surface oxide film; in a cross-section of the plating layer, a projection length L_i of an Fe-Al-Si phase in which the Si content in the Fe₂Al₅ phase is 5-20 mass% and an equivalent circle diameter is 2 μm or more, and a length L₀ of the surface of the steel base material satisfy ΣL_i/L₀≤0.70; the Mg content in the surface oxide film is 0.05 atom% or more; and the adhesion amount of the plating layer is 20 g/m² or more per surface.

Description

Hot stamped compact

The present invention relates to a hot stamped body.

In recent years, the automotive industry has been seeking to reduce the weight of vehicle bodies in order to improve fuel efficiency. In order to achieve both a lighter vehicle body and crashworthiness, one effective method is to increase the strength of the steel plates used in structural components, etc., and against this background, the development of high-strength steel plates is underway.

Hot stamping is known as a technique for press-forming difficult-to-form materials such as high-strength steel plates. Hot stamping is a hot forming technique in which the material to be formed is heated and then shaped. With this technique, the material is heated before being shaped, so the steel is soft and has good formability when formed. Therefore, even high-strength steel can be precisely formed into complex shapes, and because the material is quenched at the same time as it is formed using a press die, the steel is known to have sufficient strength after forming.

In relation to this, various studies are being conducted on hot stamped bodies with Al-containing plating and plated steel sheets for such hot stamped bodies.

For example, Patent Document 1 describes a steel sheet coated with a metal coating having an Al/Zn ratio of greater than 2.9, comprising 2.0-24.0 wt. % zinc, 7.1-12.0 wt. % silicon, optional 1.1-8.0 wt. % magnesium, and optional additional elements selected from Pb, Ni, Zr, or Hf, with the weight content of each additional element being less than 0.3 wt. %, the balance being aluminum and optional unavoidable impurities and residual elements. Patent Document 1 also teaches that metal coatings having an Al/Zn ratio of greater than 2.9 have high sacrificial protection.

Patent Document 2 describes an aluminum alloy plated steel sheet that includes a base steel sheet and an aluminum alloy plated layer formed on the base steel sheet, the aluminum alloy plated layer containing, by weight, 21-35% Zn, 1-6.9% Si, 2-12% Fe, the balance being Al and other unavoidable impurities. Patent Document 2 also teaches that weldability and corrosion resistance can be ensured by controlling the Al/(Zn+Si) of the aluminum alloy plated layer to 1.3-2.6.

Special table 2018-528324 publication Special Publication No. 2022-550142

For example, when plated steel sheets as described in Patent Documents 1 and 2, more specifically plated steel sheets containing a relatively large amount of Al as a component in the plated layer, are used in hot stamp forming, the plated layer and the base steel (base steel sheet) may be alloyed during heating in the hot stamp forming, resulting in a decrease in corrosion resistance.

The present invention aims to provide a hot stamped body having an Al-containing plating layer that has improved corrosion resistance even after hot stamping.

In order to achieve the above object, the present inventors have conducted research, focusing particularly on the chemical composition and structure of the coating layer. As a result, the present inventors have found that excellent corrosion resistance can be achieved in a hot stamped body by forming a coating layer made of an Al-Zn- _Mg -Si system coating in a coating weight of at least a predetermined amount, forming a coating layer after hot stamping mainly of an _Fe2Al5 phase _, an Fe-Al phase formed on the _Fe2Al5 phase and having a relatively low Fe content, and _a surface oxide film modified with Mg, and further appropriately controlling the morphology of the _Fe2Al5 phase, thereby completing the present invention.

The present invention, which has achieved the above object, is as follows.
(1) A steel plate having a plating layer disposed on a surface of the steel plate,
The chemical composition of the plating layer is, in mass%,
Zn: 2.5-40.0%,
Si: 0.05-15.0%,
Fe: 25.0-40.0%,
Mg: 0.005-3.000%,
Ni: 0 to 0.500%,
Ca: 0-3.000%,
Sb: 0 to 0.500%,
Pb: 0 to 0.500%,
Cu: 0 to 1.000%,
Sn: 0-1.000%,
Ti: 0 to 1.000%,
Cr: 0-1.000%,
Nb: 0 to 1.000%,
Zr: 0 to 1.000%,
Mn: 0 to 1.000%,
Mo: 0-1.000%,
Ag: 0-1.000%,
Li: 0 to 1.000%,
La: 0 to 0.500%,
Ce: 0-0.500%,
B: 0 to 0.500%,
Y: 0 to 0.500%,
Sr: 0-0.500%,
In: 0 to 0.500%,
Co: 0 to 0.500%,
Bi: 0-0.500%,
P: 0 to 0.500%,
W: 0 to 0.500%, and the balance: Al and impurities,
The total content of Ni, Ca, Sb, Pb, Cu, Sn, Ti, Cr, Nb, Zr, Mn, Mo, Ag, Li, La, Ce, B, Y, Sr, In, Co, Bi, P, and W is 5.000% or less;
the plating layer includes, in order from the steel base material side, _{an Fe2Al5} phase, an Fe-Al phase having an Fe content of 20 to 40 mass %, and a surface oxide film;
In a cross section of the coating layer, a projected length L _i of an Fe-Al-Si phase having a Si content of 5 to 20 mass % in the Fe ₂ Al ₅ phase and an equivalent circle diameter of 2 μm or more and a length L ₀ of the surface of the steel base material satisfy ΣL _i /L ₀ ≦0.70,
The Mg content in the surface oxide film is 0.05 atomic % or more,
1. A hot stamped product, characterized in that the coating weight of the plating layer is 20 g/m2 or ^more per side.
(2) The chemical composition of the plating layer is, in mass%,
Contains Zn: 5.0 to 35.0% and Si: 0.25 to 6.0%;
The hot stamped steel according to (1) above, characterized in that the Mg content in the surface oxide film is 0.30 atomic % or more.
(3) The hot stamped steel according to (1) or (2) above, characterized in that ΣL _i /L ₀ ≦0.50.

The present invention makes it possible to provide a hot stamped body having an Al-containing plating layer that has improved corrosion resistance even after hot stamping.

FIG. 1 is an example of a schematic cross-sectional view of a surface portion of a hot stamped steel according to an embodiment of the present invention, showing the projected length L _i of an Fe—Al—Si phase and the length L ₀ of the surface of a steel base material.

<Hot stamped body>
A hot stamped steel according to an embodiment of the present invention comprises a steel base material and a plating layer disposed on a surface of the steel base material,
The chemical composition of the plating layer is, in mass%,
Zn: 2.5-40.0%,
Si: 0.05-15.0%,
Fe: 25.0-40.0%,
Mg: 0.005-3.000%,
Ni: 0 to 0.500%,
Ca: 0-3.000%,
Sb: 0 to 0.500%,
Pb: 0 to 0.500%,
Cu: 0 to 1.000%,
Sn: 0-1.000%,
Ti: 0 to 1.000%,
Cr: 0-1.000%,
Nb: 0 to 1.000%,
Zr: 0 to 1.000%,
Mn: 0 to 1.000%,
Mo: 0-1.000%,
Ag: 0-1.000%,
Li: 0 to 1.000%,
La: 0 to 0.500%,
Ce: 0-0.500%,
B: 0 to 0.500%,
Y: 0 to 0.500%,
Sr: 0-0.500%,
In: 0 to 0.500%,
Co: 0 to 0.500%,
Bi: 0-0.500%,
P: 0 to 0.500%,
W: 0 to 0.500%, and the balance: Al and impurities,
The total content of Ni, Ca, Sb, Pb, Cu, Sn, Ti, Cr, Nb, Zr, Mn, Mo, Ag, Li, La, Ce, B, Y, Sr, In, Co, Bi, P, and W is 5.000% or less;
the plating layer includes, in order from the steel base material side, _{an Fe2Al5} phase, an Fe-Al phase having an Fe content of 20 to 40 mass %, and a surface oxide film;
In a cross section of the coating layer, a projected length L _i of an Fe-Al-Si phase having a Si content of 5 to 20 mass % in the Fe ₂ Al ₅ phase and an equivalent circle diameter of 2 μm or more and a length L ₀ of the surface of the steel base material satisfy ΣL _i /L ₀ ≦0.70,
The Mg content in the surface oxide film is 0.05 atomic % or more,
The plating layer is characterized in that the coating weight per side is 20 g/ ^m2 or more.

As mentioned above, when a plated steel sheet containing a relatively large amount of Al as a component in the plated layer is used in hot stamp forming, the plated steel sheet and the base steel (base steel sheet) are alloyed during heating in the hot stamp forming, which may reduce the corrosion resistance. To explain in more detail, for example, when a plated steel sheet having a plated layer made of a conventional Al-Si-based plating is hot stamp formed, the plated steel sheet and the base steel sheet are alloyed during high-temperature heating in the hot stamp forming (for example, heating at about 900°C or higher), and a plated steel sheet containing mainly the Fe ₂ Al ₅ phase is formed after hot stamp forming. However, in addition to the Fe ₂ Al ₅ phase, a relatively large amount of Fe-Al-based intermetallic compounds containing relatively large amounts of Si, particularly Fe-Al-Si phases containing 5 mass% or more of Si, may also be formed in the plated steel sheet. In such a case, bimetallic corrosion (galvanic corrosion) may occur between the Fe ₂ Al ₅ phase and the Fe-Al-Si phase, which may reduce the corrosion resistance of the hot stamped body.

Therefore, the present inventors conducted a study, focusing in particular on the chemical composition and form of the plating layer made of Al-Si-based plating before hot stamping, in order to provide a hot stamped body having an Al-containing plating layer having excellent corrosion resistance even after hot stamping. As a result, the present inventors found that by appropriately preparing a plating layer made of Al-Zn-Mg-Si-based plating in which Zn and Mg are further added to the Al-Si plating and by appropriately selecting the heat treatment conditions for hot stamping, it is possible to suppress the formation of an Fe-Al-Si phase that may cause galvanic corrosion between the Fe ₂ Al ₅ phase in the plating layer formed after hot stamping, thereby improving the corrosion resistance of the formed body after hot _stamping . Furthermore, the present inventors found that the red rust resistance of the hot stamped body can be improved by forming an _Fe -Al phase having a relatively low Fe content, more specifically, an Fe content of 20 to 40 mass %, on the Fe 2 Al 5 phase. In addition, the present inventors have found that the addition of Mg makes it possible to appropriately modify the surface oxide film in the plating layer after hot stamp forming, thereby improving the chemical conversion treatability of the hot stamped body.

More specifically, the present inventors first found that by setting the coating weight of the coating layer made of Al-Zn-Mg-Si-based coating to 20 g/ ^m2 or more per side and further appropriately selecting the heat treatment conditions for hot stamp forming, it is possible to form an Fe _- Al phase having a lower Fe content than the _Fe2Al5 phase on the _{Fe2Al5 phase} on the steel base material side without alloying the entire coating layer to the _{Fe2Al5 phase} during high-temperature heating in hot stamp forming. To explain in more detail, during high-temperature heating in hot stamp forming, Fe from the steel base material diffuses into the coating layer and is alloyed with Al, but by making the coating weight of the coating layer relatively large and appropriately weakening the degree of alloying, it is possible to form an Fe _- Al phase having a lower Fe content than the _Fe2Al5 phase, i.e., an Fe _- Al phase having an Fe content of 20 to ₄₀ mass %, on the surface side of the coating layer, although a sufficiently alloyed Fe2Al5 phase is formed on the steel base material side of the coating layer. Without intending to be bound by any particular theory, it is believed that the improvement in red rust resistance due to the Fe-Al phase is due to the fact that the Fe-Al phase is less alloyed than the _Fe2Al5 phase _.

Next, the present inventors have found that, as will be described in detail later in relation to the manufacturing method of a hot stamped body, by containing a predetermined amount of Si in the Fe-Al phase corresponding to the interface alloy layer formed at the interface between the base steel sheet and the coating layer before hot stamping, more specifically, by containing 3.0 mass% or more of Si in the interface alloy layer, it is possible to suppress the formation of a relatively large Fe-Al-Si phase in the Fe ₂ Al ₅ phase in the coating layer formed after hot stamping. More specifically, the present inventors have found that, in the coating layer after hot stamping, the relatively large Fe-Al-Si phase in the Fe ₂ Al ₅ phase formed on the steel base metal side of the coating layer is dispersed and present, that is, by controlling the projected length L _i of the Fe-Al-Si phase having a Si content of 5 to 20 mass% and a circle equivalent diameter of 2 μm or more and the length L ₀ of the surface of the steel base metal to satisfy ΣL _i /L ₀ ≦0.70, the corrosion resistance of the coating layer after hot stamping can be significantly improved.

Fig. 1 is an example of a schematic cross-sectional view of a surface portion of a hot stamped steel according to an embodiment of the present invention, showing the projected length L _i of the Fe-Al-Si phase and the length L ₀ of the surface of the steel base material. Referring to Fig. 1, a hot stamped steel 1 according to an embodiment of the present invention includes a steel base material 2 and a coating layer 3 disposed on the surface of the steel base material 2, and the coating layer 3 includes, in order from the steel base material 2 side, an Fe ₂ Al ₅ phase 4 located on the steel base material 2, an Fe-Al phase 5 located on the Fe ₂ Al ₅ phase 4, more specifically, an Fe-Al phase 5 having an Fe content of 20 to 40 mass%, and a surface oxide film 6. In Fig. 1, an Fe _- Al-Si phase ₇ having a Si content of 5 to 20 mass% and a circle equivalent diameter of 2 µm or more is present in the Fe 2 Al 5 phase 4. Here, the sum ΣL _i of the projected lengths L _i of each Fe-Al-Si phase 7 projected onto the surface of the steel base material 2 (in FIG. 1, ΣL _i = L ₁ + L ₂ + L ₃ ) and the length L ₀ of the surface of the steel base material 2 satisfy ΣL _i /L ₀ ≦0.70, and therefore the relatively large Fe-Al-Si phase 7 is dispersed and present in the Fe ₂ Al ₅ phase 4. When the projected lengths of the multiple Fe-Al-Si phases 7 overlap partially, the entire projected length including the overlapping portion is determined as one projected length. If the Fe-Al-Si phase 7 is present in a layered form in the Fe ₂ Al ₅ phase 4, it is considered that when galvanic corrosion occurs at the contact portion between the layered Fe-Al-Si phase 7 and the Fe ₂ Al ₅ phase 4, the corrosion will progress along the contact interface. As a result, the corrosion resistance of the plating layer 3 is significantly reduced. In contrast, in the hot stamped steel 1 according to the embodiment of the present invention, the Fe-Al-Si phase 7 is dispersed in the Fe ₂ Al ₅ phase 4 so as to satisfy ΣL _i /L ₀ ≦0.70, so that even if galvanic corrosion occurs at a contact portion between one or more Fe-Al-Si phases 7 and the Fe ₂ Al ₅ phase 4 present therearound, the corrosion will not progress from the corrosion at the contact portion to other Fe-Al-Si phases 7, thereby making it possible to significantly improve the corrosion resistance of the coating layer 3. In addition, in the hot stamped steel 1 according to the embodiment of the present invention, Zn is dissolved in the Fe ₂ Al ₅ phase 4 and the Fe-Al phase 5 in association with the addition of Zn to the coating layer, and therefore the corrosion resistance is further improved by the sacrificial anticorrosive action of Zn.

In addition, in Fig. 1, Mg is present in the surface oxide film 6 in an amount of 0.05 atomic % or more, and it is considered that the presence of Mg can modify the surface oxide film, thereby improving the chemical conversion treatability of the hot stamped body. To explain in more detail, Mg is generally present in the plating layer as an _Mg2Si phase or the like. On the other hand, since the plating layer 3 of the hot stamped body 1 according to the embodiment of the present invention contains a relatively large amount of Al, its surface is covered with an oxide film composed of Al-containing oxides and the like. Here, since the _Mg2Si phase has a relatively high melting point, it is difficult to be oxidized even during high-temperature heating in hot stamping, and therefore it is considered that it cannot act on the oxide film composed of Al-containing oxides and the like to modify the oxide film. In response to this, the present inventors have found that, as will be described in detail later in relation to the manufacturing method of a hot stamped body, by appropriately controlling the cooling after plating, it is possible to form an Mg-Al-Zn-Si intermetallic compound phase having a lower melting point and a tendency to be easily oxidized compared to the Mg ₂ Si phase in the plating layer before hot stamp forming, more specifically, an Mg-Al-Zn-Si intermetallic compound phase having an Al content of 10 mass % or more, and that the presence of the Mg-Al-Zn-Si intermetallic compound phase is effective in modifying the surface oxide film. As described above, the Mg-Al-Zn-Si intermetallic compound phase has a lower melting point and a tendency to be easily oxidized compared to the Mg ₂ Si phase. Therefore, the Mg-Al-Zn-Si intermetallic compound phase melts during high-temperature heating in hot stamp forming, and the dissolved Mg can be introduced into the Al-containing oxide present on the surface in an amount of 0.05 atomic % or more. As a result, the oxide film formed on the surface of the formed body during hot stamp forming can be appropriately modified by Mg, which is believed to improve the chemical conversion treatability of the resulting hot stamped body. In general, when the chemical conversion treatability is reduced, a region where the chemical conversion coating is not formed, called a "sk", may be generated, and in such a case, the corrosion resistance after painting is reduced. In other words, by improving the chemical conversion treatability of the hot stamped body, it is possible to improve the corrosion resistance of the hot stamped body after painting.

Therefore, according to the hot stamped steel according to the embodiment of the present invention, it is possible to achieve excellent corrosion resistance by combining the effect of suppressing the formation of the Fe-Al- _Si phase 7 that may cause galvanic corrosion between the _Fe 2 Al 5 phase 4, more specifically, the effect of suppressing the progress of corrosion obtained by dispersing and forming a relatively large Fe-Al-Si phase 7, the effect of improving red rust resistance due to the formation of the Fe-Al phase 5, and the effect of improving chemical conversion treatability due to the modification of the surface oxide film by Mg. In particular, the fact that the corrosion resistance of the hot stamped steel 1 can be improved by forming the coating layer 3 from the Fe ₂ Al ₅ phase 4, the Fe _- Al phase 5 having a relatively low Fe content, and the surface oxide film 6 modified by Mg, and further by appropriately controlling the form of the Fe 2 Al ₅ phase 4 as described above, was revealed for the first time by the present inventors. Therefore, the hot stamped steel according to the embodiment of the present invention is particularly useful in the automotive field where hot stamping is relatively often used.

The hot stamped body according to an embodiment of the present invention will be described in more detail below. In the following description, the unit of content of each element, "%", means "mass%" unless otherwise specified. Furthermore, in this specification, "to" indicating a numerical range is used to mean that the numerical values before and after it are included as the lower and upper limits, unless otherwise specified.

[Plating layer]
According to an embodiment of the present invention, the plating layer is disposed on the surface of the steel base material, for example, disposed on at least one, preferably both, surfaces of the steel base material. Here, the expression "disposed on the surface of the steel base material" includes not only the case where the plating layer is directly disposed on the surface of the steel base material, but also the case where the plating layer is indirectly disposed on the surface of the steel base material, for example, the case where a solid solution layer, which will be described later, is included between the steel base material and the plating layer. The plating layer has the following chemical composition.

[Zn: 2.5-40.0%]
Zn has a sacrificial anticorrosive effect and is an element effective in improving the corrosion resistance of the plating layer. In addition, Zn reacts with the treatment liquid during chemical conversion treatment to form a chemical conversion coating on the surface. In order to fully obtain these effects, the Zn content is set to 2.5% or more. The Zn content may be 3.5% or more, 5.0% or more, 8.0% or more, 10.0% or more, 12.0% or more, 15.0% or more, 18.0% or more, 20.0% or more, or 22.0% or more. On the other hand, if Zn is excessively contained, the melting of Zn during high-temperature heating in hot stamp forming becomes significant, and the molten Zn may penetrate into the steel and cause liquid metal embrittlement (LME) cracking. Therefore, the Zn content is set to 40.0% or less. The Zn content may be 38.0% or less, 35.0% or less, 32.0% or less, 30.0% or less, or 28.0% or less.

[Si: 0.05-15.0%]
Si is an element effective in improving the adhesion of the plating layer. In order to fully obtain such an effect, the Si content is set to 0.05% or more. The Si content may be 0.1% or more, 0.2% or more, 0.25% or more, 0.3% or more, 0.5% or more, 0.8% or more, 1.0% or more, 3.0% or more, or 5.0% or more. On the other hand, if Si is contained excessively, the formation of the Fe-Al-Si phase in the Fe ₂ Al ₅ phase becomes significant, and the corrosion resistance may decrease. Therefore, the Si content is set to 15.0% or less. The Si content may be 12.0% or less, 10.0% or less, 8.0% or less, or 6.0% or less.

[Fe:25.0-40.0%]
When a plated steel sheet is heated during hot stamp forming, Fe from the steel base material diffuses into the plated layer and is alloyed with Al, etc., so that the plated layer inevitably contains Fe. Therefore, the Fe content is 25.0% or more, and may be, for example, 26.0% or more, 28.0% or more, 30.0% or more, or 32.0% or more. On the other hand, if the Fe content is too high, the red rust resistance may be reduced due to excessive alloying of the plated layer. Therefore, the Fe content is 40.0% or less, and may be, for example, 38.0% or less, 36.0% or less, or 34.0% or less.

[Mg: 0.005-3.000%]
Mg is an element effective in improving the corrosion resistance, particularly chemical conversion treatability, of the coating layer. In order to fully obtain such an effect, the Mg content is set to 0.005% or more. The Mg content may be 0.010% or more, 0.020% or more, 0.030% or more, 0.050% or more, 0.080% or more, 0.100% or more, or 0.300% or more. On the other hand, from the viewpoint of improving workability, the Mg content is set to 3.000% or less. The Mg content may be 2.500% or less, 2.000% or less, 1.500% or less, 1.000% or less, 0.800% or less, 0.600% or less, or 0.400% or less.

Furthermore, the plating layer may optionally contain Ni: 0-0.500%, Ca: 0-3.000%, Sb: 0-0.500%, Pb: 0-0.500%, Cu: 0-1.000%, Sn: 0-1.000%, Ti: 0-1.000%, Cr: 0-1.000%, Nb: 0-1.000%, Zr: 0-1.000%, Mn: 0-1.000%, Mo: 0-1.000 %, Ag: 0-1.000%, Li: 0-1.000%, La: 0-0.500%, Ce: 0-0.500%, B: 0-0.500%, Y: 0-0.500%, Sr: 0-0.500%, In: 0-0.500%, Co: 0-0.500%, Bi: 0-0.500%, P: 0-0.500%, and W: 0-0.500% may be contained. The total content of these optional elements (i.e., the total content of these elements) is 5.000% or less. The total content of the optional elements may be 4.500% or less, 4.000% or less, 3.500% or less, 3.000% or less, 2.500% or less, 2.000% or less, 1.500% or less, 1.000% or less, 0.800% or less, 0.500% or less, 0.100% or less, or 0.050% or less. The inclusion of these elements is not essential, and the total content of these elements may be 0%. If necessary, the lower limit of the total content of these elements may be 0.001%, 0.010%, 0.050%, or 0.080%. These optional elements will be described in detail below.

[Ni: 0-0.500%]
Ni is an element effective for improving the corrosion resistance of the plating layer. The Ni content may be 0%, but in order to obtain such an effect, the Ni content is preferably 0.001% or more. The Ni content may be 0.003% or more, 0.005% or more, 0.008% or more, 0.010% or more, or 0.020% or more. Although there is no particular upper limit, from the viewpoint of manufacturing costs, etc., the Ni content is set to 0.500% or less, and may be, for example, 0.400% or less, 0.300% or less, 0.100% or less, 0.050% or less, or 0.030% or less.

[Ca: 0-3.000%]
Ca is an element effective in ensuring wettability of the plating bath. The Ca content may be 0%, but in order to obtain such an effect, the Ca content is preferably 0.001% or more. The Ca content may be 0.003% or more, 0.005% or more, or 0.010% or more. On the other hand, if Ca is contained excessively, a large amount of hard intermetallic compounds may be formed in the plating layer, making the plating layer brittle and reducing the adhesion to the steel sheet. Therefore, the Ca content is preferably 3.000% or less. The Ca content may be 2.000% or less, 1.000% or less, 0.500% or less, 0.300% or less, 0.100% or less, 0.050% or less, or 0.020% or less.

[Sb: 0 to 0.500%, Pb: 0 to 0.500%, Cu: 0 to 1.000%, Sn: 0 to 1.000%, Ti: 0 to 1.000%, Cr: 0 ~1.000%, Nb: 0-1.000%, Zr: 0-1.000%, Mn: 0-1.000%, Mo: 0-1.000%, Ag: 0-1.000 %, Li: 0-1.000%, La: 0-0.500%, Ce: 0-0.500%, B: 0-0.500%, Y: 0-0.500%, Sr: 0- 0.500%, In: 0 to 0.500%, Co: 0 to 0.500%, Bi: 0 to 0.500%, P: 0 to 0.500% and W: 0 to 0.500%]
Sb, Pb, Cu, Sn, Ti, Cr, Nb, Zr, Mn, Mo, Ag, Li, La, Ce, B, Y, Sr, In, Co, Bi, P and W may not be contained in the plating layer, but may be present in the plating layer in an amount of 0.0001% or more, 0.001% or more, or 0.01% or more. These elements do not adversely affect the performance of the hot stamped body as long as they are within a predetermined content range. However, if the content of each element is excessive, the corrosion resistance may be reduced. Therefore, the content of Sb, Pb, La, Ce, B, Y, Sr, In, Co, Bi, P and W is preferably 0.500% or less, and may be, for example, 0.300% or less, 0.100% or less, 0.050% or less, or 0.020% or less. Similarly, the contents of Cu, Sn, Ti, Cr, Nb, Zr, Mn, Mo, Ag and Li are preferably 1.000% or less, and may be, for example, 0.800% or less, 0.500% or less, 0.100% or less, 0.050% or less, or 0.020% or less.

The remainder of the plating layer other than the above elements consists of Al and impurities. Impurities in the plating layer are components that are mixed in due to various factors in the manufacturing process, including raw materials, when the plating layer is manufactured. The Al content does not need to be specified in particular, but may be 10.0 to 72.45%. If necessary, the Al content may be 20.0% or more, 25.0% or more, 30.0% or more, 35.0% or more, 38.0% or more, 40.0% or more, or 42.0% or more, or 70.0% or less, 65.0% or less, 60.0% or less, 57.0% or less, 54.0% or less, 51.0% or less, or 48.0% or less.

[Measurement of chemical composition of plating layer]
The chemical composition of the plating layer is determined by dissolving only the plating layer in an acidic aqueous solution and chemically analyzing it. That is, the plating layer is dissolved in an acidic aqueous solution at room temperature containing an inhibitor that inhibits the dissolution of steel, for example, an acidic aqueous solution at room temperature containing 10% hydrochloric acid and 0.04% IBIT 710K (manufactured by Asahi Chemical Industry Co., Ltd.), and the resulting acidic aqueous solution is analyzed by ICP (inductively coupled plasma atomic emission spectroscopy) to obtain the chemical composition of the plating layer.

[ _{Fe2Al5 phase} ]
[ΣL _i /L ₀ ≦0.70]
In an embodiment of the present invention, the coating layer contains an _{Fe2Al5 phase} on the steel base metal side, and the projected length L _i of the Fe _- Al- _Si phase having a Si content of 5-20 mass% and a circle equivalent diameter of 2 μm or more in the Fe2Al5 phase and the length L ₀ of the surface of the steel base metal are controlled to satisfy ΣL _i /L ₀ ≦0.70. As described above, the Fe-Al-Si phase having a Si content of 5-20 mass% may cause galvanic corrosion between the _Fe2Al5 phase and the _Fe2Al5 phase. In particular, if the Fe-Al-Si phase is relatively large and exists continuously in a layered or nearly layered form, corrosion will progress along the contact interface between the Fe-Al- _Si phase and the _Fe2Al5 phase, and the corrosion resistance of the coating layer will be significantly reduced. Therefore, in order to suppress the progress of such corrosion and improve the corrosion resistance of the coating layer, it is necessary to have the Fe-Al-Si phase having a circle equivalent diameter of 2 μm or more dispersed in the Fe ₂ Al ₅ phase. Therefore, in the embodiment of the present invention, as shown in FIG. 1, the Fe-Al-Si phase is dispersed in the Fe 2 Al 5 phase so that the sum ΣL _i of the projected lengths L _i of each Fe-Al-Si phase having a circle equivalent diameter of 2 μm or more projected onto the surface of the steel base material and the length L ₀ of the surface of the steel base material 2 satisfy ΣL _i /L ₀ ≦ _0.70 , thereby improving the corrosion resistance of the _coating layer. From the viewpoint of further improving the corrosion resistance improvement effect, the lower the value of ΣL _i /L ₀ , the more preferable, and it may be, for example, 0.65 or less, 0.60 or less, 0.55 or less, 0.50 or less, 0.45 or less, or 0.40 or less.

On the other hand, even if corrosion occurs in the Fe-Al-Si phase having a circle equivalent diameter of less than 2 μm, the corrosion does not proceed further from the corrosion to other Fe-Al-Si phases. Therefore, even if an Fe-Al-Si phase having a circle equivalent diameter of less than 2 μm exists, it does not necessarily have a detrimental effect on the corrosion resistance of the hot stamped body. In this regard, from the viewpoint of further improving the corrosion resistance, the Fe-Al-Si phase having a circle equivalent diameter of 2 μm or more may not exist in the Fe ₂ Al ₅ phase. That is, the lower limit of ΣL _i /L ₀ may be 0. Although not particularly limited, for example, ΣL _i /L ₀ may be 0.05 or more, 0.10 or more, 0.15 or more, or 0.20 or more.

[Fe-Al phase having an Fe content of 20 to 40 mass %]
In an embodiment of the present invention, the plating layer includes an Fe _- Al phase having a lower Fe content than the Fe _{2 Al 5 phase} (Fe content: more than 40 to 60 mass%), i.e., an Fe-Al phase having an Fe content of 20 to 40 mass%, on the surface side of the Fe 2 Al 5 phase. The Fe-Al phase having an Fe content of 20 to 40 mass% has a lower degree of alloying than the Fe ₂ Al ₅ phase, and in this regard, can contribute to improving red rust resistance. The Si content in the Fe-Al phase is less than 5 mass%. In this specification, the Fe-Al phase having an Fe content of 20 to 40 mass% may be simply referred to as the Fe-Al phase.

[Mg content in surface oxide film: 0.05 atomic % or more]
In an embodiment of the present invention, as shown in FIG. 1, the plating layer includes a surface oxide film on its surface, and the Mg content in the surface oxide film is controlled to 0.05 atomic % or more. Since the plating layer of the hot stamped body according to the embodiment of the present invention contains a relatively large amount of Al, the surface is covered with an oxide film composed of Al-containing oxides and the like. By introducing Mg into such a surface oxide film in an amount of 0.05 atomic % or more, the surface oxide film can be appropriately modified, thereby improving the chemical conversion treatability of the hot stamped body. From the viewpoint of further enhancing the effect of improving the chemical conversion treatability, the higher the Mg content in the surface oxide film, the more preferable it is, and it may be, for example, 0.10 atomic % or more, 0.20 atomic % or more, 0.30 atomic % or more, 0.50 atomic % or more, 0.80 atomic % or more, 1.00 atomic % or more, or 1.50 atomic % or more. On the other hand, even if the surface oxide film contains an excessive amount of Mg, the above effect is saturated. Therefore, although not particularly limited, the Mg content in the surface oxide film is preferably 6.00 atomic % or less, and may be, for example, 5.50 atomic % or less, 5.00 atomic % or less, 4.50 atomic % or less, or 4.00 atomic % or less.

[Analysis of plating layer]
The plating layer is analyzed as follows. First, five samples are taken from the hot stamped body so that the cross section of the plating layer can be observed. Next, for each sample, a rectangular range of 80 μm in the thickness direction and 100 μm in the direction perpendicular to the thickness direction is defined as one visual field, and five visual fields in total for the five samples are photographed at a magnification of 1500 times using SEM-EDS or EPMA to obtain a mapping image. From the element distribution image of this mapping image, the positions of the Fe-Al phase having an Fe content of 20 to 40 mass%, the Fe ₂ Al ₅ phase, and the Fe _- Al-Si phase having a Si content of 5 to 20 mass% and a circle equivalent diameter of 2 μm or more present inside the Fe 2 Al ₅ phase, as well as the surface oxide film, are determined. More specifically, an element distribution image is obtained by SEM-EDS or EPMA with the measurement target elements being Fe, Al, Si, and Zn. In this element distribution image, the region that satisfies Fe: 20-40 mass% and Al: 58-78 mass% is defined as the Fe-Al phase having an Fe content of 20-40 mass%. The concentration range of the color bar showing the concentration of each element in the element distribution image by color tone is set to Fe: 20-40 mass% and Al: 58-78 mass%, and the Fe-Al phase having an Fe content of 20-40 mass% (reference numeral 5 in FIG. 1) is specified by superimposing the element distribution images of Fe and Al with the color bar adjusted. In this element distribution image, the region that satisfies Fe: more than 40 to 60 mass%, Al: 40 to less than 60 mass%, Si: 0 to less than 5 mass%, and Zn: 0 to 15 mass% is defined as the Fe ₂ Al ₅ phase (reference numeral 4 in FIG. 1). The region in which the Si content is 5 to 20 mass% and the circle equivalent diameter is 2 μm or more and is surrounded by the Fe ₂ Al ₅ phase is defined as the Fe-Al-Si phase (reference numeral 7 in FIG. 1). Next, the Fe-Al-Si phase is projected onto the surface of the steel base material using image analysis software (for example, the "Analyze" function of "ImageJ"), and the sum of the projected lengths L _i of each Fe-Al-Si phase (L ₁ +L ₂ +L ₃ in FIG. 1) is calculated. Finally, the average of the sums of L _i obtained for the five samples is calculated as ΣL _i , and the ratio ΣL _i /L ₀ to the length L ₀ of the corresponding steel base material surface (length of the long side in each field: 100 μm) is calculated. Here, L ₀ , which is the length of the long side in the field, is also the distance between both ends of the measurement region (field) as shown in FIG. 1 (however, the distance in the direction parallel to the surface of the hot stamped body 1).

The Mg content in the surface oxide film is determined by measuring the concentration of elements constituting the surface oxide film for each of the five samples using SEM-EDS or EPMA, and averaging the measured values of the target element concentration for the five samples. More specifically, first, in each sample, the area that satisfies O: 30-70 mass%, Al: 30-70 mass%, and Mg: 0-2.5 mass% in the measurement by SEM-EDS or EPMA is determined to be the surface oxide (reference number 6 in Figure 1). Next, in each sample, the Mg content is measured at five measurement points spaced 50 μm apart in the direction parallel to the surface of the hot stamped body at the center position of the thickness of the area identified as the surface oxide, and the average value is determined to be the Mg content of each sample. The average value of the Mg contents in the five samples is determined to be the Mg content in the surface oxide film.

The plating layer having _the above chemical composition, _Fe2Al5 phase, Fe-Al phase, and surface oxide film may be a hot-dip plating layer. It is not necessary to exclude plating layers other than the hot-dip plating layer, but it may be limited to the hot-dip plating layer.

[Plating layer deposition weight: 20 g/ ^m2 or more per side]
In the hot stamped product according to the embodiment of the present invention, the coating weight of the coating layer is 20 g/m ² or more per side. In general, the coating layer may be alloyed with the steel base material during high-temperature heating in hot stamp forming, resulting in a decrease in corrosion resistance. However, according to the embodiment of the present invention, by making the coating weight of the coating layer relatively large, specifically 20 g/m ² or more per side, while appropriately weakening the degree of alloying, a sufficiently alloyed Fe ₂ Al ₅ phase is formed on the steel base material side of the coating layer, but an Fe-Al phase having a lower Fe content than the Fe ₂ Al ₅ phase, that is, an Fe-Al phase having an Fe content of 20 to 40 mass %, can be formed on the surface side of the coating layer. On the other hand, if the coating weight of the coating layer is small, the alloying of the coating layer may proceed too much during high-temperature heating in hot stamp forming, making it impossible to form an Fe-Al phase having a relatively low Fe content. In this case, the effect of improving red rust resistance due to the formation of an Fe-Al phase cannot be obtained. Alternatively, if the coating weight of the plating layer is small, the effect of adding Zn having a sacrificial anticorrosive effect to the plating layer may not be fully obtained, and in this case, the corrosion resistance after hot stamp forming is reduced. From the viewpoint of improving corrosion resistance, the coating weight of the plating layer is preferably 30 g/m ² or more, 40 g/m 2 or more, or 50 g/m ² or more, more preferably 60 g/m ² or more, even more preferably 70 g/m ² or ^more , and most preferably 80 g/m ² or more per side. Although there is no particular upper limit, the coating weight of the plating layer may be, for example, 200 g/m ² or less, 190 g/m ² or less, 180 g/m ² or less, or 170 g/m ² or less.

[Measurement of plating weight]
The coating weight of the plating layer is determined by dissolving only the plating layer in an acidic aqueous solution. That is, a 30 mm x 30 mm sample is taken from the hot stamped body, and then dissolved in an acidic aqueous solution containing an inhibitor that inhibits the dissolution of steel, for example, 0.04% Ibit 710K (manufactured by Asahi Chemical Industry Co., Ltd.) in 10% hydrochloric acid.
The plating layer is dissolved in an acidic aqueous solution at room temperature to which has been added, and the amount of plating layer attached is determined from the change in mass of the sample before and after dissolution of the plating layer.

[Solid solution layer]
In an embodiment of the present invention, the hot stamped product may further include a solid solution layer between the steel base material and the plating layer. Depending on the plating composition before hot stamping and the hot stamping conditions, a solid solution may be formed between Fe diffusing from the steel base material to the plating layer and Al and/or Zn in the plating layer, and a solid solution layer containing a solid solution of these elements may be formed between the steel base material and the plating layer after hot stamping. Therefore, when the hot stamped product further includes a solid solution layer, the solid solution layer contains Fe and one or both of Al and Zn. More specifically, the solid solution layer includes an Fe-Al solid solution layer, an Fe-Zn solid solution layer, and/or an Fe-Al-Zn solid solution layer.

The presence of a solid solution layer can be confirmed as follows. First, the plating layer alone is dissolved in an acidic aqueous solution containing an inhibitor that inhibits the dissolution of steel, specifically, 10% hydrochloric acid plus 0.04% Ivit 710K (manufactured by Asahi Chemical Industry Co., Ltd.) at room temperature. Next, using a high-frequency glow discharge optical emission spectrometer (GDS), the surface of the hot stamped compact is placed in an Ar atmosphere, and a voltage is applied to generate glow plasma, and the surface of the hot stamped compact is sputtered and analyzed in the depth direction. Then, the elements contained in the material are identified from the element-specific emission spectrum wavelengths emitted by excited atoms in the glow plasma, and the emission intensity of the identified elements is estimated. The data in the depth direction can be estimated from the sputtering time. Specifically, the relationship between sputtering time and sputtering depth is obtained in advance using a standard sample, so that the sputtering time can be converted to sputtering depth. Therefore, the sputtering depth converted from the sputtering time can be defined as the depth from the surface of the material. The obtained emission intensity is converted to mass% by creating a calibration curve. When the hot stamped body is subjected to GDS measurement in this manner, the region in the depth direction where the Al concentration is greater than 1.00 mass% and is 1.10 times or more the Al content of the steel base material is determined to be the solid solution layer.

[Preferable chemical composition of steel base material]
As described above, the present invention aims to provide a hot stamped product having an Al-containing plating layer having improved corrosion resistance even after hot stamp forming, and the object is achieved by optimizing the chemical composition and coating weight of the plating layer made of an Al-Zn-Mg-Si-based plating, configuring the plating layer mainly with an Fe ₂ Al ₅ phase, an Fe-Al phase formed on the Fe ₂ Al ₅ phase and having a relatively low Fe content, and a surface oxide film modified with Mg, and controlling the projected length L _i of the Fe-Al-Si phase having a Si content of 5 to 20 mass% and a circle equivalent diameter of 2 μm or more in the _{Fe 2} Al ₅ phase and the length L ₀ of the surface of the steel base material so as to satisfy ΣL _i /L ₀ ≦0.70. Therefore, it is clear that the chemical composition of the steel base material itself is not an essential technical feature for achieving the object of the present invention. Hereinafter, preferred chemical compositions of the steel base material used in the hot stamped body according to the embodiment of the present invention will be described in detail. However, these descriptions are intended to merely exemplify preferred chemical compositions of the steel base material for the hot stamped body, and are not intended to limit the present invention to the use of a steel base material having such a specific chemical composition.

In an embodiment of the present invention, for example, the steel base material comprises, in mass %,
C: 0.13-0.50%,
Si: 0.001 to 3.000%,
Mn: 0.30-3.00%,
Al: 0.0002-2.000%,
P: 0.100% or less,
S: 0.1000% or less,
N: 0.0100% or less,
Nb: 0 to 0.15%,
Ti: 0 to 0.15%,
V: 0 to 0.15%,
Mo: 0-1.0%,
Cr: 0-1.0%,
Cu: 0 to 1.0%,
Ni: 0-1.0%,
B: 0 to 0.0100%,
W: 0-1.000%,
Hf: 0 to 0.050%,
Mg: 0 to 0.050%,
Zr: 0 to 0.050%,
Ca: 0-0.010%,
REM: 0-0.30%,
It is preferable that the chemical composition is Ir: 0 to 1.000%, and the balance: Fe and impurities. Each element will be described in more detail below.

[C:0.13-0.50%]
C is an element that inexpensively increases tensile strength and is an important element for controlling the strength of steel. In order to fully obtain such an effect, the C content is preferably 0.13% or more. The C content may be 0.15% or more, 0.20% or more, 0.30% or more, or 0.35% or more. On the other hand, excessive C content may cause a decrease in elongation. For this reason, the C content is preferably 0.50% or less. The C content may be 0.45% or less, or 0.40% or less.

[Si: 0.001 to 3.000%]
Si acts as a deoxidizer and is an element that suppresses the precipitation of carbides during the cooling process during cold-rolled sheet annealing. In order to fully obtain such effects, the Si content is preferably 0.001% or more. The Si content may be 0.010% or more, 0.100% or more, or 0.200% or more. On the other hand, excessive Si content may increase the steel strength and decrease the elongation. For this reason, the Si content is preferably 3.000% or less. The Si content may be 2.500% or less, 2.000% or less, 1.500% or less, or 1.000% or less.

[Mn: 0.30-3.00%]
Mn is an element that enhances the hardenability of steel and is effective in increasing strength. In order to fully obtain such an effect, the Mn content is preferably 0.30% or more. The Mn content may be 0.50% or more, 1.00% or more, or 1.30% or more. On the other hand, excessive Mn content may increase the steel strength and decrease the elongation. For this reason, the Mn content is preferably 3.00% or less. The Mn content may be 2.80% or less, 2.50% or less, or 2.00% or less.

[Al: 0.0002-2.000%]
Al acts as a deoxidizer for steel and is an element that has the effect of improving the soundness of steel. In order to fully obtain such an effect, the Al content is preferably 0.0002% or more. The Al content may be 0.001% or more, 0.010% or more, 0.050% or more, or 0.100% or more. On the other hand, if Al is contained excessively, coarse Al oxides may be generated and the elongation of the steel sheet may decrease. For this reason, the Al content is preferably 2.000% or less. The Al content may be 1.500% or less, 1.000% or less, 0.800% or less, or 0.500% or less.

[P: 0.100% or less]
P is an element that segregates at grain boundaries and promotes embrittlement of steel. Since the lower the P content, the better, it is ideally 0%. However, excessive reduction in the P content may lead to a significant increase in costs. For this reason, the P content may be 0.0001% or more, or may be 0.001% or more, or 0.005% or more. On the other hand, excessive inclusion of P may lead to embrittlement of steel due to grain boundary segregation as described above. Therefore, the P content is preferably 0.100% or less. The P content may be 0.050% or less, 0.030% or less, or 0.010% or less.

[S: 0.1000% or less]
S is an element that generates nonmetallic inclusions such as MnS in steel, which leads to a decrease in the ductility of steel parts. The lower the S content, the better, so ideally it is 0%. However, excessive reduction in the S content may lead to a significant increase in costs. For this reason, the S content may be 0.0001% or more, 0.0002% or more, 0.0010% or more, or 0.0050% or more. On the other hand, excessive S content may lead to the occurrence of cracks originating from nonmetallic inclusions during cold forming. Therefore, the S content is preferably 0.1000% or less. The S content may be 0.0500% or less, 0.0200% or less, or 0.0100% or less.

[N: 0.0100% or less]
N is an element that forms coarse nitrides in the steel sheet and reduces the workability of the steel sheet. Since the lower the N content, the more preferable it is, the ideal N content is 0%. However, excessive reduction in the N content may lead to a significant increase in manufacturing costs. For this reason, the N content may be 0.0001% or more, 0.0005% or more, or 0.0010% or more. On the other hand, excessive N content may form coarse nitrides as described above, thereby reducing the workability of the steel sheet. Therefore, the N content is preferably 0.0100% or less. The N content may be 0.0080% or less, or 0.0050% or less.

The preferred basic chemical composition of the steel base material is as described above. Furthermore, the steel base material may contain, as necessary, one or more elements selected from the group consisting of Nb: 0-0.15%, Ti: 0-0.15%, V: 0-0.15%, Mo: 0-1.0%, Cr: 0-1.0%, Cu: 0-1.0%, Ni: 0-1.0%, B: 0-0.0100%, W: 0-1.000%, Hf: 0-0.050%, Mg: 0-0.050%, Zr: 0-0.050%, Ca: 0-0.010%, REM: 0-0.30%, and Ir: 0-1.000%, in place of a portion of the remaining Fe. Each of these elements may be 0.0001% or more, 0.0005% or more, 0.001% or more, or 0.01% or more.

The remainder of the steel base material other than the above elements consists of Fe and impurities. Impurities in steel base material are components that are mixed in due to various factors in the manufacturing process, including raw materials such as ore and scrap, when the steel base material is industrially manufactured.

The chemical composition of the steel base material may be measured by a general analytical method. For example, the chemical composition of the steel base material may be measured by first removing the plating layer by mechanical grinding, and then using ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrometry) on the cutting chips in accordance with JIS G 1201:2014. Specifically, for example, a 35 mm square test piece may be obtained from the vicinity of the 1/2 position of the plate thickness of the steel base material, and the composition may be identified by measuring it under conditions based on a calibration curve created in advance using a Shimadzu ICPS-8100 or similar (measuring device). C and S, which cannot be measured by ICP-AES, may be measured using the combustion-infrared absorption method, N may be measured using the inert gas fusion-thermal conductivity method, and O may be measured using the inert gas fusion-non-dispersive infrared absorption method.

[Thickness of hot stamped body]
The thickness of the hot stamped steel is not particularly limited, and may be, for example, 0.2 mm or more, 0.3 mm or more, 0.6 mm or more, 1.0 mm or more, or 2.0 mm or more. Similarly, the thickness of the hot stamped steel may be, for example, 6.0 mm or less, 5.0 mm or less, or 4.0 mm or less.

<Method of Manufacturing Hot Stamped Product>
Next, a preferred method for producing the hot stamped steel according to the embodiment of the present invention will be described. The following description is intended to exemplify a characteristic method for producing the hot stamped steel according to the embodiment of the present invention, but is not intended to limit the hot stamped steel to one produced by the production method described below.

The hot stamped product according to an embodiment of the present invention can be manufactured by, for example, carrying out a casting process in which molten steel with an adjusted chemical composition is cast to form a slab, a hot rolling process in which the slab is hot rolled to obtain a hot rolled steel sheet, a coiling process in which the hot rolled steel sheet is coiled, a cold rolling process in which the coiled hot rolled steel sheet is cold rolled to obtain a cold rolled steel sheet, an annealing process in which the cold rolled steel sheet is annealed, a cooling process in which the annealed cold rolled steel sheet is cooled, a plating process in which a plating layer is formed on the obtained steel base material, and a hot stamp forming process in which the obtained plated steel sheet is hot stamp formed. Alternatively, the cold rolling process may be carried out directly after pickling without coiling after the hot rolling process. Each process will be described in detail below.

[Casting process]
The conditions for the casting process are not particularly limited. For example, after melting in a blast furnace or an electric furnace, various secondary smelting processes may be carried out, and then casting may be carried out by a method such as ordinary continuous casting or casting by an ingot method.

[Hot rolling process]
The cast slab is hot-rolled to obtain a hot-rolled steel sheet. The hot-rolling step is performed by reheating the cast slab directly or after cooling and then hot-rolling it. When reheating is performed, the heating temperature of the slab may be, for example, 1100 to 1250°C. In the hot-rolling step, rough rolling and finish rolling are usually performed. The temperature and reduction of each rolling step can be appropriately determined according to the desired metal structure and plate thickness. For example, the end temperature of the finish rolling may be 900 to 1050°C, and the reduction of the finish rolling may be 10 to 50%.

[Winding process]
The hot-rolled steel sheet can be coiled at a predetermined temperature. The coiling temperature can be appropriately determined depending on the desired metal structure, etc., and may be, for example, 500 to 800°C. The hot-rolled steel sheet may be subjected to a predetermined heat treatment by recoiling before or after coiling. Alternatively, the coiling step may be omitted, and the hot-rolled steel sheet may be pickled after the hot-rolling step and then subjected to the cold-rolling step described later.

[Cold rolling process]
After the hot-rolled steel sheet is subjected to pickling or the like, the hot-rolled steel sheet is cold-rolled to obtain a cold-rolled steel sheet. The rolling reduction in the cold rolling can be appropriately determined according to the desired metal structure and sheet thickness, and may be, for example, 20 to 80%. After the cold rolling step, the steel sheet may be cooled to room temperature, for example, by air cooling.

[Annealing process]
Next, the obtained cold-rolled steel sheet is annealed. The annealing step includes heating the cold-rolled steel sheet to a temperature of 730 to 900 ° C. in an atmosphere with a dew point of -50 to 20 ° C. and holding the temperature for 10 to 300 seconds. In particular, by carrying out the annealing step under conditions of a relatively high dew point of -10 to 20 ° C., the surface layer of the cold-rolled steel sheet can be appropriately decarburized. In this case, although the reason is not necessarily clear, it is possible to make the Fe-Al-Si phase more dispersed in the Fe ₂ Al ₅ phase in the coating layer of the finally obtained hot stamped body. As a result, the value of ΣL _i /L ₀ can be reduced compared to the case where the annealing step is carried out under conditions of a dew point of less than -10 ° C., and for example, ΣL _i /L ₀ can be reduced to 0.50 or less, and the corrosion resistance after hot stamping can be further improved. The atmosphere in the annealing step may be a reducing atmosphere, more specifically a reducing atmosphere containing nitrogen and hydrogen, for example a reducing atmosphere of 1 to 10% hydrogen (eg, 4% hydrogen and the balance nitrogen).

[Cooling process]
The cooling step may be performed at a cooling rate suitable for obtaining a desired metal structure from the heating temperature of the annealing step to the entry sheet temperature of the subsequent plating step. Although not particularly limited, for example, the cooling step may be performed at an average cooling rate of 10° C./s or more from the heating temperature of the annealing step to the entry sheet temperature of the plating step.

[Plating process]
Next, in the plating step, a plating layer is formed on at least one, preferably both, surfaces of the cold-rolled steel sheet (steel base material). More specifically, the plating step is carried out using a plating bath having a predetermined chemical composition, for example, a plating bath containing Zn: 5.0 to 50.0%, Si: 0.1 to 18.0%, Mg: 0.010 to 3.000%, and the balance: Al and impurities (plating bath temperature: 650°C or higher, for example, 650 to 680°C), so that the temperature of the steel base material entering the plating bath is 500°C or lower, and after plating, the steel is primarily cooled to 480°C at an average cooling rate of 20°C/s or higher, and then secondary cooled from 480°C to 300°C at an average cooling rate of 10°C/s or lower. The plating step is important for obtaining a desired chemical composition of the Fe-Al phase corresponding to the interface alloy layer formed at the interface with the steel base material, and is also important for forming an Mg-Al-Zn-Si-based intermetallic compound phase in the plating layer. This will be explained in detail below.

Generally, the plating process is carried out so that the entry sheet temperature is the same as or approximately the same as the plating bath temperature. However, if the difference between the entry sheet temperature of the steel base material into the plating bath and the plating bath temperature (i.e., plating bath temperature - entry sheet temperature) is less than 150°C, if the entry sheet temperature is higher than 500°C, or if the plating bath temperature is lower than 650°C, it becomes impossible to form an appropriate phase type of Fe-Al phase. Specifically, in these cases, the Si content of the Fe-Al phase becomes less than 3.0%. As a result, when such a plated steel sheet is subjected to high-temperature heating (hot stamp forming), it becomes impossible to sufficiently suppress the formation of the Fe-Al-Si phase in the Fe ₂ Al ₅ phase during the high-temperature heating. In this case, the value of ΣL _i /L ₀ becomes large, and the corrosion resistance of the plating layer after hot stamp forming is greatly reduced. Therefore, in the present manufacturing method, the plating bath temperature is controlled to 650°C or more and the entry sheet temperature is controlled to 500°C or less to ensure that the entry sheet temperature is 150°C or more lower than the plating bath temperature, thereby crystallizing the interface alloy layer (Fe-Al phase) at a low temperature and changing the phase type to one suitable for containing 3.0 mass% or more of Si in the interface alloy layer. It is considered that by containing 3.0 mass% or more of Si in the interface alloy layer, it is possible to trap much of the Si present in the plating layer before hot stamp forming in the interface alloy layer. Since the Fe-Al-Si phase after hot stamp forming is an intermetallic compound containing a relatively large amount of Si, it is considered that by trapping much of Si in the interface alloy layer before hot stamp forming, it is possible to suppress the formation of the Fe-Al-Si phase in the Fe ₂ Al ₅ phase during high-temperature heating in hot stamp forming. As a result, it is believed possible to manufacture a hot stamped steel in which the Fe--Al--Si phase is dispersed in the Fe ₂ Al ₅ phase so as to satisfy ΣL _i /L ₀ ≦0.70.

Generally, the entry sheet temperature is controlled to be the same as or to the same extent as the plating bath temperature as described above, and even if the entry sheet temperature is different from the plating bath temperature, the entry sheet temperature is generally controlled within a range of ±20°C relative to the plating bath temperature. The reason for this is that, although the sheet temperature rises to the plating bath temperature when immersed in the plating bath, there is no need to take the manufacturing cost to cool and control the entry sheet temperature to a lower temperature, and the plating bath may solidify due to the entry sheet temperature being lower than the plating bath temperature. Therefore, it is quite unexpected and surprising that the corrosion resistance of the plating layer after hot stamp forming can be improved by controlling the plating bath temperature to 650°C or higher and the entry sheet temperature to 500°C or lower, as in this manufacturing method, to ensure that the entry sheet temperature is 150°C or lower than the plating bath temperature. The lower limit of the entry sheet temperature is not particularly limited, but for example, the entry sheet temperature of the steel base material into the plating bath may be 380°C or higher. Conventional wisdom would suggest that controlling the entry sheet temperature to 500°C or less could lead to the plating bath solidifying due to its composition. However, in this embodiment, it has been discovered that by setting the difference between the entry sheet temperature and the plating bath temperature to 150°C or more, which is significantly greater than conventional wisdom, that is, by setting the entry sheet temperature to 500°C or less and setting the plating bath temperature to a high temperature of 650°C, it is possible to prevent the plating bath from solidifying. In order to prevent the plating bath from solidifying, it is preferable to circulate the plating solution by stirring the plating bath.

The plating process is carried out, for example, by hot-dip plating. Other conditions of the plating process may be appropriately set in consideration of the thickness and adhesion amount of the plating layer. For example, a cold-rolled steel sheet is immersed in a plating bath, then pulled out, and immediately sprayed with _N2 gas or air by a gas wiping method, and then cooled, so that the adhesion amount of the plating layer can be adjusted to a predetermined range, for example, within the range of 20 to 200 g/ ^m2 per side.

[Cooling after plating]
As described above, the plated steel sheet is primarily cooled to 480°C at an average cooling rate of 20°C/s or more, and then secondary cooled from 480°C to 300°C at an average cooling rate of 10°C/s or less. By cooling the plated steel sheet based on such a combination of primary cooling at a relatively fast average cooling rate (20°C/s or more) and secondary cooling at a relatively slow average cooling rate (10°C/s or less), it is possible to form an Mg-Al-Zn-Si intermetallic compound phase in the plated layer. To explain in more detail, when Mg is added during plating, the Mg ₂ Si phase is generally likely to crystallize. However, first, in the primary cooling, the plated steel sheet is rapidly cooled to 480°C at an average cooling rate of 20°C/s or more, so that the composition of the liquid phase can be made suitable for the crystallization of the Mg- _Al -Zn-Si intermetallic compound phase while suppressing the crystallization of the Mg 2 Si phase. Next, in the secondary cooling, the steel sheet is slowly cooled from 480°C to 300°C at an average cooling rate of 10°C/s or less, whereby the Mg-Al-Zn-Si intermetallic compound phase can be stably and slowly crystallized, and it is possible to form a plating layer containing 0.010% or more of the Mg-Al-Zn-Si intermetallic compound phase with an Al content of 10% or more by area ratio in the plating layer. The Mg-Al-Zn-Si intermetallic compound phase with an Al content of 10% or more by mass has a relatively low melting point and is easily oxidized. For this reason, by containing 0.010% or more of the Mg-Al-Zn-Si intermetallic compound phase by area ratio in the plating layer, the Mg-Al-Zn-Si intermetallic compound phase can be dissolved during high-temperature heating in hot stamp forming, and the oxide film formed on the surface of the formed body during hot stamp forming can be appropriately modified by the dissolved Mg. As a result, the Mg content in the surface oxide of the obtained hot stamped body becomes 0.05 atomic % or more, making it possible to improve the chemical conversion treatability of the hot stamped body.

On the other hand, if the material is rapidly cooled from 480°C to 300°C or cooled at an average cooling rate of more than 10°C/s, the liquid phase composition becomes suitable for the crystallization of the α-(Al, Mg, Zn) phase, i.e., Mg is dissolved in the α-Al phase, and the desired amount of Mg-Al-Zn-Si intermetallic compound phase cannot be crystallized. In this case, it is natural that the oxide film formed on the surface of the formed body during high-temperature heating in hot stamp forming cannot be modified by Mg, and as a result, the Mg content in the surface oxide becomes less than 0.05 atomic %, and the desired chemical conversion treatability cannot be obtained. The upper limit of the average cooling rate for the primary cooling is not particularly limited, but may be, for example, 50°C/s or less. Similarly, the lower limit of the secondary cooling is not particularly limited, but may be, for example, 3°C/s or more.

[Hot stamp forming process]
Finally, the obtained plated steel sheet is hot stamped in a hot stamp forming process to produce a hot stamped body including a desired plated layer. From the viewpoint of obtaining a desired plated layer, it is preferable to load the plated steel sheet into a furnace at 800 to 1000°C, and hold the plated steel sheet in the furnace for 5 to 50 seconds after the temperature of the plated steel sheet reaches a predetermined temperature, for example, 900°C. If the holding time is 50 seconds or more, the alloying of the plated steel layer progresses too much, and it may become impossible to form an Fe-Al phase having a relatively low Fe content. The heating atmosphere is not particularly limited, and may be under normal conditions, for example, in air, a gas combustion atmosphere with a controlled ratio of air to fuel, or a nitrogen atmosphere, and the dew point may be controlled in these gases. Examples of the heating method include electric heating, high-frequency heating, and induction heating. After heating and holding in the furnace, the plated steel sheet is removed from the furnace, and then the plated steel sheet reaches a predetermined temperature, for example, a predetermined temperature of 850°C or less, and hot stamp forming can be performed under normal conditions. After hot stamp forming, the material may be cooled to a temperature range of, for example, 250° C. or lower at an average cooling rate of 20° C./sec or higher, although this is not particularly limited.

According to this manufacturing method, it is possible to manufacture a hot stamped body in which the chemical composition of the entire coating layer is controlled within a predetermined range, the coating weight of the coating layer is 20 g/m ² _or more per side, the coating layer is mainly composed of an Fe ₂ Al ₅ phase, an Fe-Al phase formed on _the Fe ₂ Al ₅ phase and effective for improving red rust resistance, and a surface oxide film modified with Mg, and further, the Fe-Al-Si phase in the Fe ₂ Al ₅ phase is dispersed so as to satisfy ΣL _i /L ₀ ≦0.70. Therefore, it is possible to significantly improve the corrosion resistance of the hot stamped body by combining the effect of inhibiting the progress of corrosion obtained by dispersing and forming the Fe-Al-Si phase in the Fe 2 Al 5 phase, the effect of improving red rust resistance due to the formation of the Fe-Al phase, and the effect of improving chemical conversion treatability due to the modification of the surface oxide film by Mg. Therefore, according to such a hot stamped body, it is possible to realize superior corrosion resistance compared to conventional hot stamped bodies. This will contribute to industrial development by extending the service life of automobiles and building materials.

The present invention will be described in more detail below with reference to examples. However, the following examples are merely examples of the present invention, and the present invention is in no way limited to these examples. It goes without saying that the present invention can be modified as desired without departing from the gist of the present invention.

In the following examples, hot stamped bodies according to embodiments of the present invention were manufactured under various conditions, and the properties of the manufactured hot stamped bodies were investigated.

First, molten steel was cast by continuous casting to form a slab having a chemical composition by mass of C: 0.20%, Si: 0.012%, Mn: 1.30%, Al: 0.030%, P: 0.005%, S: 0.0020%, and N: 0.0030%, with the balance being Fe and impurities. The slab was once cooled, then reheated to 1200°C and hot rolled, and then coiled at a temperature of 600°C or less. The hot rolling was performed by rough rolling and finish rolling, with the finishing temperature of the finish rolling being 900-1050°C and the reduction ratio of the finish rolling being 30%. Next, the obtained hot-rolled steel sheet was pickled and then cold rolled at a reduction ratio of 50% to obtain a cold-rolled steel sheet having a thickness of 1.6 mm. Next, the obtained cold-rolled steel sheet was subjected to an annealing process under the conditions shown in Table 1 in a mixed gas atmosphere of 4% hydrogen and the balance of nitrogen in a furnace with an oxygen concentration of 20 ppm or less, and then cooled at an average cooling rate of 10°C/s or more to produce a steel base material.

Next, the produced steel base material was cut into 100 mm x 200 mm, and the steel base material was plated using a batch-type hot-dip plating test device manufactured by our company. More specifically, the produced steel base material was first introduced into a plating bath having various chemical compositions and plating bath temperatures shown in Table 1 at the entry sheet temperature shown in Table 1 and immersed for about 3 seconds, then pulled up at a pulling speed of 20 to 200 mm/s, and the coating weight of the plating layer was adjusted to the value shown in Table 1 by _N2 gas wiping. Next, the steel base material with the plating layer attached was primarily cooled to 480°C at the average cooling rate shown in Table 1 using nitrogen gas as a cooling gas, and then secondarily cooled from 480°C to 300°C at the average cooling rate shown in Table 1, thereby obtaining a plated steel sheet with a plating layer formed on both sides of the steel base material. The sheet temperature was measured using a thermocouple spot-welded to the center of the steel base material.

[Chemical composition analysis of plating layer, etc.]
The chemical composition of the plating layer after hot stamp forming was determined as follows. First, the plated steel sheet was heated by electrical heating, and after the temperature of the plated steel sheet reached 900°C, it was held for 10 seconds. Next, the plated steel sheet was removed from the furnace, and the plated steel sheet was sandwiched between flat plate dies at about room temperature and quenched to obtain a hot stamped body having a plating layer including, from the steel base metal side, an Fe ₂ Al ₅ phase, an Fe-Al phase having an Fe content of 20 to 40 mass%, and a surface oxide film. The plated layer of the sample cut into 30 mm x 30 mm of the hot stamped body after heating and quenching was dissolved in an acidic aqueous solution at room temperature containing 10% hydrochloric acid and 0.04% IBIT 710K (manufactured by Asahi Chemical Industry Co., Ltd.), and the obtained acid solution was measured by ICP emission spectroscopy to determine the chemical composition of the plating layer. In addition, the mass of the sample before and after the pickling and peeling was measured, and the adhesion amount of the plating layer was determined from the change in mass. The results are shown in Table 1.

[Structural analysis of plating layer]
_{The Fe2Al5} phase, the Fe-Al phase having an Fe content of 20 to 40 mass%, the Fe-Al-Si phase having an Si content of 5 to 20 mass% and an equivalent circle diameter of 2 μm or more, and the surface oxide film were identified by the above-mentioned method, and the Mg content of the surface oxide film was determined by the above-mentioned method. Furthermore, the value of ΣL _i /L ₀ was determined by the above-mentioned method. Note that, except for the example that did not have an Fe-Al phase having an Fe content of 20 to ₄₀ mass% (specifically, Comparative Example 40), the _Fe2Al5 phase, the Fe-Al phase having an Fe content of 20 to 40 mass%, and the surface oxide film were present in this order from the side of the steel base material.

[Red rust resistance]
The red rust resistance after hot stamp forming was evaluated as follows. First, the plated steel sheet was heated by electrical heating, and after the temperature of the plated steel sheet reached 900°C, it was held for 10 seconds. Next, the plated steel sheet was removed from the furnace, and the plated steel sheet was sandwiched between flat molds at about room temperature and quenched. A sample of the hot stamp formed body after heating and quenching, 50 mm x 100 mm, was subjected to Zn phosphate treatment (SD5350 system: Nippon Paint Industrial Coating Co., Ltd. standard), and then electrocoating (PN110 Powernics Gray: Nippon Paint Industrial Coating Co., Ltd. standard) was performed at 20 μm, and baking treatment was performed at a temperature of 150°C and 20 minutes. Next, a cut reaching the base steel (steel base material) was introduced into the center of the sample. Next, a neutral salt spray cycle test as specified in JIS H 8502:1999, 8.1 was carried out to measure the number of cycles until red rust was generated from the cut portion, and the corrosion resistance was evaluated as follows.
A: 3 or more cycles B: Less than 3 cycles

[Chemical conversion treatment properties]
The chemical conversion treatability was evaluated as follows. First, the plated steel sheet was heated by electrical heating, and after the temperature of the plated steel sheet reached 900°C, it was held for 10 seconds. Next, the plated steel sheet was removed from the furnace, and the plated steel sheet was sandwiched between flat molds at about room temperature and quenched. A sample of 50 mm x 100 mm of the hot stamped body after heating and quenching was subjected to Zn phosphate treatment (SD5350 system: standard manufactured by Nippon Paint Industrial Coating Co., Ltd.) to form a chemical conversion coating. Next, the P intensity was measured by fluorescent X-ray analysis, and the calibration curve was used to convert it into the adhesion amount of the chemical conversion coating. The chemical conversion treatability of the hot stamped body was evaluated according to the following evaluation criteria according to the adhesion amount of the chemical conversion coating.
AA: Adhesion amount 0.9 g/ ^m2 or more A: Adhesion amount 0.1 to less than 0.9 g/ ^m2 B: Adhesion amount less than 0.1 g/ ^m2

[Paint blister]
The coating blister was evaluated as follows. First, a sample of 50 mm x 100 mm of the hot stamped body after heating and quenching in the same manner as in the case of red rust resistance was subjected to Zn phosphate treatment (SD5350 system: Nippon Paint Industrial Coating Co., Ltd. standard), then electrocoating (PN110 Powernics Gray: Nippon Paint Industrial Coating Co., Ltd. standard) was performed at 20 μm, and baking treatment was performed at a temperature of 150 ° C and 20 minutes. Next, a cut reaching the base steel (steel base material) was introduced in the center of the sample. Next, a neutral salt spray cycle test specified in 8.1 of JIS H 8502:1999 was performed for 120 cycles to measure the coating blister width, and the corrosion resistance was evaluated as follows.
AAA: 2mm or less AA: More than 2 to 3mm
A: More than 3 to 4 mm
B: More than 4 mm

　If the red rust resistance rating was A, the chemical conversion treatability ratings were AA and A, and the paint blister ratings were AAA, AA and A, the hot stamped body was evaluated as having an Al-containing plating layer with improved corrosion resistance even after hot stamping. The results are shown in Table 1.

With reference to Table 1, in Comparative Example 32, it is considered that the desired Si content was not obtained in the interface alloy layer in the coating layer before hot stamp forming because the entry sheet temperature in the coating process was high. As a result, the formation of the Fe-Al-Si phase in the Fe ₂ Al ₅ phase in the coating layer after hot stamp forming became significant, the value of ΣL _i /L ₀ became large, and the corrosion resistance after hot stamp forming deteriorated. In Comparative Example 33, it is considered that the average cooling rate in the primary cooling from after coating to 480°C was slow, so that a large amount of Mg ₂ Si phase was formed in the coating layer before hot stamp forming, and the Mg-Al-Zn-Si intermetallic compound phase could not be sufficiently formed. As a result, Mg could not be sufficiently introduced into the surface oxide after hot stamp forming, and the chemical conversion treatability deteriorated. In Comparative Example 34, since the average cooling rate in the secondary cooling from 480°C to 300°C was fast, most of the Mg in the plating layer before hot stamp forming was dissolved in the α-Al phase, and it is considered that the Mg-Al-Zn-Si intermetallic compound phase could not be sufficiently formed. As a result, Mg could not be sufficiently introduced into the surface oxide after hot stamp forming, and the chemical conversion treatability was reduced. In Comparative Example 35, since the Zn content in the plating layer was low, the reaction with phosphoric acid did not proceed sufficiently during the chemical conversion treatment, and the chemical conversion treatability was reduced. In Comparative Example 36, since the Si content in the plating layer was high, the formation of the Fe-Al-Si phase became significant, the value of ΣL _i /L ₀ became large, and the corrosion resistance after hot stamp forming was reduced. In Comparative Example 37, since the Si content in the plating layer was low, the adhesion of the plating layer was reduced, and the corrosion resistance after hot stamp forming was reduced. In Comparative Example 38, since the Mg content in the plating layer was low, Mg could not be sufficiently introduced into the surface oxide after hot stamp forming, and the chemical conversion treatability was reduced. In Comparative Example 39, since the adhesion amount of the plating layer was insufficient, the corrosion resistance after hot stamp forming was reduced. In Comparative Example 40, the Fe content in the plating layer was high due to excessive alloying, and it was not possible to form an Fe-Al phase having an Fe content of 20 to 40 mass%. As a result, the red rust resistance after hot stamp forming was reduced. In Comparative Example 41, since the plating bath temperature was low, the plating bath solidified when the steel base material was immersed in the plating bath, and the plating layer could not be properly formed. For this reason, the subsequent production was stopped, and analysis and performance evaluation were not performed.

In contrast to this, in all of the hot stamped steels according to the present invention, the chemical composition of the entire plating layer was controlled within a prescribed range, the coating weight of the plating layer was set to 20 g/ ^m2 or _more per side, the plating layer was composed mainly of an _Fe2Al5 phase, an Fe-Al phase, and a surface oxide film modified with Mg, and the Fe-Al-Si phase in _{the Fe2Al5 phase} was dispersed so as to satisfy ΣL _i /L ₀ ≦0.70. As a result, even when exposed to a high temperature of 900°C, the corrosion resistance of the hot stamped steel was significantly improved by a combination of the corrosion progression inhibition effect obtained by dispersing and forming an Fe-Al-Si phase in the _Fe2Al5 phase, the effect of improving red rust resistance due to the formation of the Fe-Al phase, and the effect of improving chemical conversion treatability due to the modification of the surface oxide film with Mg. In addition, for the plated steel sheets according to all the Examples before hot stamp forming, the cross sections of the plated layers were measured for element concentration by EPMA, and the Si content in the interface alloy layer was higher than that in Comparative Example 32, being 3.0 mass% or more in all the Examples. In addition, for the plated layers according to all the Examples before hot stamp forming, the element distribution images of the mapping images obtained by EPMA were measured, and it was found that the Mg-Al-Zn-Si-based intermetallic compound phase having an Al content of 10 mass% or more was contained in the plated layer in an amount significantly exceeding 0.010% in terms of area ratio. On the other hand, in Comparative Examples 33 and 34, the Mg-Al-Zn-Si-based intermetallic compound phase was not contained in the plated layers before hot stamp forming. In particular, in Examples 27 to 31 in which the chemical composition of the entire plating layer contained 5.0 to 35.0% Zn and 0.25 to 6.0% Si, the Mg content in the surface oxide film was 0.30 atomic % or more, and the relationship ΣL _i /L ₀ ≦0.50 was satisfied, the red rust resistance was rated A, the chemical conversion treatability was rated AA, and the coating blistering was rated AAA, thereby further improving the corrosion resistance. Furthermore, when GDS measurement was performed on each hot stamped product, the presence of a solid solution layer containing an Fe-Al solid solution layer, an Fe-Zn solid solution layer, and/or an Fe-Al-Zn solid solution layer was confirmed between the steel base material and the plating layer in the hot stamped products of all the Examples.

REFERENCE SIGNS LIST 1 Hot stamped body 2 Steel base material 3 Coating layer 4 Fe ₂ Al ₅ phase 5 Fe-Al phase having an Fe content of 20 to 40 mass % 6 Surface oxide film 7 Fe-Al-Si phase having a Si content of 5 to 20 mass % and an equivalent circle diameter of 2 μm or more

Claims (3)

A steel base material and a plating layer disposed on a surface of the steel base material,
The chemical composition of the plating layer is, in mass%,
Zn: 2.5-40.0%,
Si: 0.05-15.0%,
Fe: 25.0-40.0%,
Mg: 0.005-3.000%,
Ni: 0 to 0.500%,
Ca: 0-3.000%,
Sb: 0 to 0.500%,
Pb: 0 to 0.500%,
Cu: 0 to 1.000%,
Sn: 0-1.000%,
Ti: 0 to 1.000%,
Cr: 0-1.000%,
Nb: 0 to 1.000%,
Zr: 0 to 1.000%,
Mn: 0 to 1.000%,
Mo: 0-1.000%,
Ag: 0-1.000%,
Li: 0 to 1.000%,
La: 0 to 0.500%,
Ce: 0-0.500%,
B: 0 to 0.500%,
Y: 0 to 0.500%,
Sr: 0-0.500%,
In: 0 to 0.500%,
Co: 0 to 0.500%,
Bi: 0-0.500%,
P: 0 to 0.500%,
W: 0 to 0.500%, and the balance: Al and impurities,
The total content of Ni, Ca, Sb, Pb, Cu, Sn, Ti, Cr, Nb, Zr, Mn, Mo, Ag, Li, La, Ce, B, Y, Sr, In, Co, Bi, P, and W is 5.000% or less;
the plating layer includes, in order from the steel base material side, _{an Fe2Al5} phase, an Fe-Al phase having an Fe content of 20 to 40 mass %, and a surface oxide film;
In a cross section of the coating layer, a projected length L _i of an Fe-Al-Si phase having a Si content of 5 to 20 mass % in the Fe ₂ Al ₅ phase and an equivalent circle diameter of 2 μm or more and a length L ₀ of the surface of the steel base material satisfy ΣL _i /L ₀ ≦0.70,
The Mg content in the surface oxide film is 0.05 atomic % or more,
A hot stamped product, characterized in that the coating weight of the plating layer per side is 20 g/m2 or ^more . The chemical composition of the plating layer is, in mass%,
Contains Zn: 5.0 to 35.0% and Si: 0.25 to 6.0%;
2. The hot stamped steel according to claim 1, wherein the surface oxide film has a Mg content of 0.30 atomic % or more. The hot stamped steel according to claim 1 or 2, characterized in that ΣL _i /L ₀ ≦0.50.

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