Technical field
[0001]The present invention relates to a hot stamping member.
The present application, to 06 May 02, 2017, claiming priority based on Japanese Patent Application No. 2017-110212, filed in Japan, the contents of which are incorporated here.
BACKGROUND
[0002]Recently, for the prevention of environmental protection and global warming, there is an increasing inhibit demand consumption of chemical fuels, this demand has affected to various manufacturing industries. For example, rather than the exception for the automobile that are essential to the day-to-day life and activities as a means of transportation, such as improvement of fuel consumption due to the weight of the vehicle body is being sought. However, since simply realize the weight reduction of the vehicle body in the vehicle may lead to a reduction in safety, are not applicable product quality. Therefore, when performing the weight of the vehicle body, it is necessary to ensure proper safety.
[0003]
　Many structures of an automobile, iron, is formed in particular steel, to reduce the weight of the steel sheet, it is important for reducing vehicle weight. Also, demand for such steel sheets, not automobile manufacturing industry alone, are similarly made in various manufacturing industries. For such requirement, if simply to reduce the weight of the steel sheet, it is conceivable to reduce the thickness of the steel sheet. However, reducing the thickness of the steel sheet leads to a decrease in the strength of the structure. Therefore, in recent years, by increasing the mechanical strength of the steel sheet, the mechanical strength capable of maintaining or enhancing steel composed structure by steel be thinner than steel that was used it previously, research development is being carried out.
[0004]
　In general, materials having a high mechanical strength, in a molding process of bending, etc., tend to shape fixability is lowered. Therefore, when processed into complex shapes, processing itself becomes difficult. As a means for solving the problems of the moldability, so-called "hot stamping method (hot pressing method, a hot pressing method, hot pressing method, die quenching method)" and the like. This hot stamping method, a material is press-formed by heating to a high temperature, and molded by press working against the softened steel sheet by heating, after molding and cooling. According to the hot stamping method, since the once softened by heating to a high temperature material can be easily press working the material. Furthermore, the quenching effect due to cooling after molding, it is possible to increase the mechanical strength of the material. Thus, this hot stamping method, the molded article is obtained having a good shape fixability and high mechanical strength.
[0005]
　However, when applying this hot stamping method the steel sheet, the members and the like which require corrosion resistance, it is necessary to the anticorrosive treatment and metallization to the member surface after machining. Therefore, surface cleaning step, surface treatment step is required, the productivity is lowered.
[0006]
　For such problems, Patent Document 1, mainly composed of Al on the surface of the steel, hot pressing for aluminum-based plated steel sheet having an Al-based metal coating containing Mg and Si are described.
[0007]
　Patent Document 2, are defined the composition of the surface of the hot stamping steel plate, AlN amount of Al-Fe alloy layer surface of the steel surface is 0.01 ~ 1 g / m 2 have been described to be .
[0008]
　Patent Document 3, the surface of the steel material, has an Al-Fe intermetallic compound layer further comprises an oxide film on the surface thereof, bcc layer having Al between the steel and the Al-Fe intermetallic compound layer It describes an automobile member is an oxide film thickness of the Al-Fe alloy layer surface after hot stamping is described. By oxidation film is heated aluminum coated steel sheet to a predetermined thickness to form a Al-Fe alloy layer to the surface layer, and a coating film defects and adhesion decrease after electrodeposition coating is suppressed, after coating discloses that to ensure the corrosion resistance.
[0009]
　However, in the hot press for aluminum-based plated steel sheet described in Patent Document 1, is not sufficient corrosion resistance after painting after hot stamping. Also, not defined with respect to composition and structure of the outermost surface, the relationship between the corrosion resistance after painting the composition and structure of the outermost surface is not revealed.
　In Patent Document 2, by the AlN amount of Al-Fe alloy layer surface with a predetermined range, an improvement is seen in the corrosion resistance after some paint, there is room for further improvement.
　As described in Patent Document 3, is not sufficient corrosion resistance after painting even control the structure and thickness of the Al-Fe alloy layer. The reason may be due to a decrease in the chemical conversion treatment agent deposition amount of reactivity reduction between the oxide film and the chemical conversion treatment agent.
　Further, in order to ensure the mechanical strength of the steel sheet, it is necessary to suppress the occurrence of pitting caused by progress corrosion in the thickness direction in a portion of the steel sheet. However, the steel sheet according to these documents, measures against pitting is not sufficient.
CITATION
Patent Document
[0010]
Patent Document 1: Japanese Patent 2003-034845 JP
Patent Document 2: Japanese Patent 2011-137210 JP
Patent Document 3: Japanese Patent 2009-293078 JP
Summary of the Invention
Problems that the Invention is to Solve
[0011]
　As described above, in the conventional art, there is a problem that can not be sufficiently ensured corrosion resistance after painting and pitting resistance of the hot stamping member.
　The present invention has been made in view of such problems, a large paint adhesion affects the corrosion resistance after painting, and to provide a hot stamp member excellent in the pitting corrosion resistance.
Means for Solving the Problems
[0012]
　Hot stamping member, when used for example in automobile parts, in automotive manufacturing process, the chemical conversion film, such as serving as a base of zinc phosphate in the electrodeposition coating film is formed, a resin-based coating on the chemical conversion film film (electrodeposition film) is formed. To increase the adhesion of the coating (electrodeposition film), in the chemical conversion coating of zinc phosphate and the like as a base film of the resin coating film, it is useful to increase the amount of precipitated zinc phosphate crystals . In the chemical conversion treatment step, a zinc phosphate concentration of phosphate in the zinc aqueous solution is zinc phosphate crystals to exceed the solubility of zinc phosphate precipitate. Here, the solubility of the zinc phosphate decreases the pH of the zinc phosphate solution is increased.
　The present inventors have found that in the chemical conversion treatment step, to increase the pH of the hot stamping member surface, elements to form an oxide bring pH increase during dissolution in water, i.e., Group 2 elements of the periodic table, and the fourth period d block element, by including a predetermined amount of oxide film layer on the hot stamp member surface was found that the coating adhesion is improved.
　Further, by containing the above element in the oxide film layer, although coating adhesion is enhanced, has also been found that in some cases not always sufficient for the pitting corrosion resistance. The present inventors have conducted further studies and found that the distribution state of the oxide film layers of the element can affect the pitting corrosion resistance.
　The present invention was made based on the above findings. It is a gist of the present invention is as follows.
[0013]
[1] hot stamp member according to one embodiment of the present invention, the steel material and, the Al-Fe intermetallic compound layer formed on the steel, the Al-Fe intermetallic compound layer oxide film layer formed on If has, one of the oxide film layer, be, Mg, Ca, Sr, Ba, are selected Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, from the group consisting of Zn or the two or more group a element, and Al, and oxygen, consists impurity, the ratio of the group a elements excluding the oxygen of the oxide film layer is 0.01 atomic% or more, at 80 atomic% or less There, the a thickness t of 0.1 ~ 10.0 [mu] m of the oxide layer, using GDS, the thickness direction from the surface, when measured with a group element of the oxide film layer, said from the surface the maximum value of the detected intensity of the a group element in a range of up to 1/3 of the thickness t, before The average value of the detected intensity of the A group element in a range from 2/3 of the thickness t to t, is 3.0 times or more.
[2] The hot stamp member according to the above [1], the maximum value of the detected intensity of the A group element is, the average value of the detected intensity of the A-group element, a 8.0 times or more it may be.
[3] The hot stamp member according to the above [1] or [2], components of the steel material, by mass%, C: 0.1 ~ 0.4% , Si: 0.01 ~ 0.60% , Mn: 0.50 ~ 3.00%, P: 0.05% or less, S: 0.020% or less, Al: 0.10% or less, Ti: 0.01 ~ 0.10%, B: 0 .0001 ~ 0.0100%, N: 0.010 % or less, Cr: 0 ~ 1.0%, Mo: 0 ~ 1.0%, wherein the remainder may be made of Fe and impurities.
[4] The hot stamp member according to the above [3], components of the steel material, in mass%, Cr: 0.01 ~ 1.0% , Mo: whereas one of 0.01 to 1.0% or both may contain.
[5] The hot stamp member according to any one of [1] to [4], wherein the Al-Fe intermetallic compound layer may contain Si.
The invention's effect
[0014]
　The present invention can provide an excellent hot stamp member adhesion (coating adherence) and pitting corrosion resistance of the electrodeposition coating film. The hot stamp member is excellent in corrosion resistance after painting.
BRIEF DESCRIPTION OF THE DRAWINGS
[0015]
FIG. 1 is a sectional schematic view of a hot stamp member according to the present embodiment.
It is a graph showing the relationship between [2] the amount of precipitated zinc phosphate crystal and the ratio of group A element of the oxide film layer.
3 is a graph showing the relationship between the deposition amount and the paint adhesion of zinc phosphate crystals.
It is a graph showing the relationship between the ratio of the group A elements [4] paint adhesion to the oxide film layer.
5 is a graph showing the relationship between the thickness of the paint adhesion to the oxide film layer.
6 is a schematic view showing an example of a manufacturing method of hot stamping member.
It was measured using a [FIG 7A] GDS, a diagram illustrating an example of distribution of group A elements of the hot stamp member according to the present embodiment (Mg).
It was measured using a [FIG 7B] GDS, a diagram illustrating an example of distribution of group A element of the comparative steels (Mg).
DESCRIPTION OF THE INVENTION
[0016]
　It will be described in detail preferred embodiments of the present invention.
　Shows a cross-sectional schematic view of hot stamping member according to the present embodiment in FIG. Figure 1 is a schematic diagram to aid in understanding the layered structure of each layer. Hot stamping member according to the present embodiment, a steel product 1, the Al-Fe intermetallic compound layer 2 formed on the steel material 1, an oxide film layer 3 formed on the Al-Fe intermetallic compound layer 2, have.
　Oxide film layer 3, and one or more group A elements of the second group element or fourth period d-block element in the periodic table, and Al, and oxygen, and a dopant. The second element in the periodic table, Be, a Mg, Ca, Sr, Ba, and the fourth period d-block elements, Sc, Ti, V, Cr , Mn, Fe, Co, Ni, Cu, Zn it is. The oxide film layer 3 comprising one or more of these as the A group element.
　Further, in the oxide film layer 3, the oxygen ratio of the group A elements to all elements except the 0.01 atomic percent or more, there is a 80 atomic% or less.
　　Further, the thickness of the oxide film layer 3 is in the range of 0.1 ~ 10.0 [mu] m.
　Then, the maximum value of the detected intensity of the A group element in a range from the surface of the oxide film layer 3 to 1 / 3t (t = oxide layer thickness), the group A elements in the range from the surface to 2t / 3 ~ t the average value of the detected intensity is 3.0 times or more.
[0017]
　In hot stamping member according to the present embodiment includes an A group element in the oxide layer 3 of the outermost layer. A group element is contained in the oxide film layer 3 in the form of primarily oxides. When such hot stamping conversion processing on the outermost surface (oxide film layer) of the member is subjected, chemical conversion treatment solution at the interface between the oxide film layer and the chemical conversion treatment solution in the oxide is present in the A group element the pH is increased, the precipitation amount of zinc phosphate crystals increases thereby. That is, so-called chemical conversion treatment is enhanced. This also, adhesion electrodeposition coating film to be electrodeposition coating after the chemical conversion treatment are improved. By increases adhesion electrodeposition coating film, improving the corrosion resistance after painting.
　Also, A group element is present in concentrated in the surface layer of the oxide film layer 3. As a result, also improved pitting corrosion resistance.
[0018]
　Hereinafter, to configure a hot stamp member according to the present embodiment, Al-Fe intermetallic compound layer 2 will be described oxide film layer 3 and the steel product 1.
[0019]
(Al-Fe intermetallic compound layer
　2) Al-Fe intermetallic compound layer 2 is formed on the surfaces of the steel 1. The Al-Fe intermetallic compound layer 2 includes the Al and Fe and impurities. Moreover, even the Al-Fe intermetallic compound layer 2 may contain Si, may contain A group element to be described later. More specifically, Al-Fe intermetallic compound layer 2, there is composed of the Al and Fe and impurities, may contain further Si and / or A group element.
　Also, the metal structure Al-Fe intermetallic compound layer 2, include one or both of the Al-Fe alloy phase or Al-Fe-Si alloy phase.
[0020]
　Al-Fe intermetallic compound layer 2 is an aluminum plated steel is formed by going through the hot stamping process. Aluminum plating steel to be original plate is a steel having an Al plating layer containing aluminum or an aluminum alloy. In hot stamping process, the Al coating layer is melted by being heated above the melting point, at the same time interdiffusion with Fe and Al between the steel product 1 and the Al plating layer, Al phase of the Al coating layer is Al- by changes to Fe alloy phase, Al-Fe intermetallic compound layer 2 is formed. If that contained Si in the Al coating layer, Al phase of the Al plating layer is changed to Al-Fe-Si alloy phase. Al-Fe melting point of the alloy phase and Al-Fe-Si alloy phase is about 1150 ° C., is higher than the upper limit of the heating temperature of the general hot stamping process, they steel material surface by the alloy phase is formed precipitated to form the Al-Fe intermetallic compound layer 2. Al-Fe alloy phase and Al-Fe-Si alloy phase is a plurality of types, when the high-temperature heating or prolonged heating, will change to a more Fe concentration of high alloy phase. Further, if the Al-Fe intermetallic compound layer 2 include A group element, group A element, an intermetallic compound, may exist in a variety of forms such as a solid solution.
[0021]
　The thickness of the Al-Fe intermetallic compound layer 2 is preferably in the range of 0.1 ~ 10.0 [mu] m, more preferably in the range of 0.5 ~ 3.0 [mu] m. The thickness of the Al-Fe intermetallic compound layer 2 by the above 0.1 [mu] m, can improve the corrosion resistance of the hot stamping member. Further, by making the following 10.0μm thickness, it can prevent cracking of the Al-Fe intermetallic compound layer. The thickness of the Al-Fe intermetallic compound layer 2, from the thickness from the interface between the Al-Fe intermetallic compound layer 2 and the steel material 1 to the surface of the oxide film layer 3, reducing the thickness of the oxide film layer 3 in can be identified. The interface between the Al-Fe intermetallic compound layer 2 and the steel material 1, for example, can be identified by observing the cross section of the Al-Fe intermetallic compound layer 2 and the steel material 1 by a scanning electron microscope. The thickness of the oxide film layer can be measured by a method described later.
[0022]
　In addition, the Al-Fe intermetallic compound layer 2, titanium nitride, silicon nitride, titanium carbide, silicon carbide, titanium oxide, silicon oxide, iron oxide, nitrides such as aluminum oxide, carbide, include particles of oxides it may be. These particles are added in order to contain the group A elements in the oxide film layer. On the other hand, these particles be present in the Al-Fe intermetallic compound layer 2, it does not directly affect the adhesion to the electrodeposited coating.
[0023]
(Oxide film layer 3)
　in the Al-Fe intermetallic surface side of the compound layer 2 of a hot stamping member (steel 1 opposite), as the outermost surface layer of the hot stamping member, an oxide film layer 3 is formed. Oxide film layer 3 is a heating process of hot stamping in the production of hot stamping member, the surface of the Al coating layer of aluminum plating steel is produced by oxidation. Oxide film layer 3 is composed of a group A element, and Al, and oxygen, and impurities. Furthermore the oxide film layer 3, may include either or both of Fe or Si. Fe, Si is part of what was contained in Al-Fe intermetallic compound layer 2, which may be mixed at the time of formation of the oxide film layer 3.
　The composition of these elements in the oxide film layer 3, EPMA from section (electron probe microanalyzer) or TEM (transmission electron microscope), by GDS (Glow Discharge Spectrometer) and the like, can be quantified. The oxide film layer 3 including the group A elements, the chemical conversion treatment of the hot stamping member (phosphating property) is improved as described below.
[0024]
　A group element contained in the oxide film layer 3, the second element in the periodic table, a fourth period d-block element. In the present embodiment, the second element in the periodic table, Be, Mg, a Ca, Sr, Ba, and the fourth period d-block elements, Sc, Ti, V, Cr , Mn, Fe, Co, Ni, Cu, is Zn. Oxide film layer 3 of hot stamping member according to the present embodiment may include at least one of these elements. A group element is part of the A group element is single element or may be present in the form of compounds other than oxides, but it is present in the form of oxide in the oxide film layer 3 It is preferred. More preferably, may substantially all of the group A elements in the oxide film layer 3 (for example, 90% or more) is present in the form of oxides. A group element is, MAl 2 O 4 : it is preferably present in the form of (M A group element). Mechanism is unknown, A group element is MAl 2 O 4 when in the form of a, pitting corrosion resistance is improved.
[0025]
　Among the oxide film layer 3, it may for elements other than A group element, are present in the form of oxides. For example, Al as aluminum oxide, and other impurities are preferably present as oxides of the impurities. Also, Si in the case that contains the Si oxide film layer is preferably present as a silicon oxide, Fe of if they contain Fe is preferably present as iron oxide. Also, A group element, Al, Si, Fe, respectively, may be included in the form of composite oxide with other elements.
[0026]
　Oxides of group A elements is classified into basic oxides. In the chemical conversion treatment step, basic oxides comprising the group A elements in the oxide film, phosphorylation conversion treatment liquid (hereinafter, referred to as the chemical conversion treatment liquid) that partially dissolves upon contact with the chemical conversion treatment raising the solution pH at the interface between the liquid and the oxide film layer. On the other hand, zinc phosphate contained in the chemical conversion treatment liquid is lowered and the solubility pH is higher, the amount of crystals is increased to precipitate. Therefore, the increase in pH at the interface between the surface of the oxide film layer and the chemical conversion treatment liquid, so that zinc phosphate crystals deposited on the surface of the oxide layer increases.
[0027]
　If improving the coating adhesion by increasing the deposition amount of zinc phosphate crystals in the chemical conversion treatment, the ratio of the group A elements for all elements except oxygen in the oxide film layer 3 is 0.01 atom% or more, 80 atom % or less. The thickness of the oxide film layer 3 is in the range of 0.01 ~ 10.0 [mu] m.
　When the thickness ratio between the oxide film layer of the group A elements in the oxide film layer 3 is described above, it is possible to more precipitate zinc phosphate crystals in the chemical conversion treatment step. Hereinafter, for improving the paint adhesion by increasing the deposition amount of zinc phosphate crystals in the chemical conversion treatment, the reason for limiting the ratio and the oxide film layer 3 having a thickness of A-group element will be described.
[0028]
　Precipitation of zinc phosphate in the case of performing chemical conversion treatment on the surface of the oxide film layer 3 of hot stamping member according to the present embodiment, 0.3 g / m 2 ~ 3.0 g / m 2 is desirably. When the amount of deposition of zinc phosphate crystals is small, the unevenness of the chemical conversion film surface is relatively small, the surface area of the resin coating film and the chemical and physical bond may zinc phosphate crystal or oxide film layer is reduced. Therefore, the paint adhesion is insufficient. On the other hand, when the amount of precipitation of zinc phosphate crystals is too large, although the surface area of the zinc phosphate crystal can bind to the resin coating film is increased, the crystal itself tends to peel from the oxide film layer surface zinc phosphate. Therefore, the paint adhesion is insufficient.
[0029]
　Further, pH of the interface between the surface and the chemical conversion treatment solution of the oxide film layer during the chemical conversion treatment is desirably a 6-10. pH is reduced precipitation amount of less than 6 and zinc phosphate crystals, the pH is too much greater than the amount deposited zinc phosphate 10.
[0030]
　Figure 2 shows the percentage of group A element other than oxygen in the oxide film layer, the relationship between the deposition amount of zinc phosphate. Further, in FIG. 3, showing the relationship between the deposition amount and the paint adhesion of zinc phosphate crystals. The proportion of the group A elements in the oxide film layer in FIG. 2, among the elements constituting the oxide film layer, a content of the A element to the total amount of elemental excluding oxygen (atomic%). Reference paint adhesion score in Figure 3, electrodeposition coating put scratched with a cutter in a grid pattern at 1mm intervals over the vertical and horizontal directions 10mm to impart samples were, after 2000hr immersed in a 60 ° C. warm water and peeled They have scored from part area ratio of. Grade 3,2,1 respectively peeling area 0% or more and less than 10%, less than 70% 10% or more, showing a 70% and 100%. Each plot shown in FIGS. 2 and 3, respectively, represent the test results of the same sample. In this sample, it is used Sr as the A group element.
[0031]
　As shown in FIG. 2, according to the proportion of the group A elements in the oxide film layer is increased, it can be seen that the deposition amount of zinc phosphate is increased. Further, as shown in FIG. 3, the precipitation amount of zinc phosphate in the chemical conversion film is 0.2 g / m 2 it can be seen that becomes a rating of 2 or less in the following. Furthermore, the precipitation amount of zinc phosphate in the chemical conversion film is 3.0 g / m 2 it can be seen that to lower the score exceeds.
[0032]
　FIG. 4 shows the percentage of group A element other than oxygen in the oxide film layer, the relation between paint adhesion. It is used Sr as the A group element. Reference paint adhesion scores in FIG 4 is the same as in FIG. As shown in FIG. 4, when the ratio of group A element is less than 0.01 atomic%, chemical conversion treatment pH rise at the interface is less likely to occur with the liquid, so the precipitation amount of zinc phosphate crystals is small, electrodeposition paint adhesion of the coating film is deteriorated. On the other hand, when the ratio of the group A elements exceeds 80 atomic%, the coating adhesion is too much amount of precipitation of zinc phosphate crystal is deteriorated.
[0033]
　Figure 5 shows the relationship between the thickness and the paint adhesion of the oxide layer. Oxide layer shown in FIG. 5 is a film containing Sr as the A element. As shown in FIG. 5, the thickness of the oxide film layer is less than 0.01 [mu] m, since the amount of contributing oxide pH rise at the interface between the chemical conversion treatment solution in the chemical conversion treatment step is small, the zinc phosphate crystals deposition amount is small, the paint adhesion of the electrodeposited coating is understood to be insufficient. The thickness of the oxide film layer becomes thicker than 10.0 [mu] m, it can be seen that the oxide film layer is a lack of coating adhesion because electrodeposited coating consisting easily peeled from the plating surface.
　Trends shown in FIGS. 1 to 5, even if you change the A group element to element other than Sr, show similar behavior.
[0034]
　From the above, more than 0.01 atomic% proportion of the group A elements except oxygen in the oxide film layer is 80 atomic% or less, when the thickness of the oxide film layer is 0.01 ~ 10.0 [mu] m , it is understood that it is possible to form a chemical conversion film containing a large amount of zinc phosphate crystals in the chemical conversion treatment step. Further, chemical conversion film containing a large amount of zinc phosphate crystals, it can be seen that excellent paint adhesion.
[0035]
　The thickness of the oxide film layer 3, EPMA from section (electron probe microanalyzer) or TEM (transmission electron microscope) can be measured by GDS and the like. The interface between the oxide film layer 3 and the Al-Fe intermetallic compound layer 2, by observing the distribution of oxygen concentration can be determined. That is, the oxide film layer 3, the oxygen concentration is higher than the Al-Fe intermetallic compound layer 2. In the present embodiment, the detection intensity of oxygen is determined to be the interface between the oxide film layer 3 and the Al-Fe intermetallic compound layer 2 a reduced position to 1/6 of the maximum value by using a GDS. Specifically, in GDS, at 0.1 second intervals in the thickness direction from the surface of the oxide film layer 3, a sputtering rate of 0.060Myuemu / sec, when measured oxygen, maximum value detection intensity of oxygen atoms 1/6 to become the measurement time of the T [sec], by multiplying the sputtering rate to T, determine the thickness of the oxide film layer 3. However, if the point where the detection intensity of oxygen atoms is 1/6 of the maximum value is more than detected, among the measurement time detection intensity becomes 1/6 of the maximum value, the longest time T [sec ] and, by multiplying the sputtering rate to T, determine the thickness of the oxide film layer 3.
[0036]
　Moreover, the abundance ratio of the group A elements in the oxide film layer 3 can be measured using a TEM (transmission electron microscope) of EDX (energy dispersive X-ray spectroscopy) function. The EDX features, among the constituent elements of the oxide film layer, determined the content of the constituent elements except for oxygen, respectively, by obtaining the sum of the content of the group A elements of which, except for the oxygen in the oxide film layer A it can be determined existence ratio of the group elements. For example, the ratio of impurities is small, the group A elements, Al, for the presence ratio of group A element when the total amount of Si and Fe is 100 atomic% by atomic%, A group in oxide film layer 3 it it can be the presence ratio of the elements.
[0037]
　As described above, by controlling the ratio of the group A elements in the oxide film layer 3 (existence ratio), thereby improving the coating adhesion. In general, if the coating is sufficiently close contact, although corrosion is prevented, the like if the flaw has entered the paint (electrodeposition film), there is a risk that pitting occurs at that position. Therefore, even a member used paint paint is desired to be excellent in pitting resistance.
　The hot stamp member according to the present embodiment, in addition to the above-described coating adhesion, for improving the pitting resistance, and controls the state of existence of group A elements in the oxide film layer 3 (distribution state).
　Specifically, by using a GDS, the thickness direction from the surface of the oxide film layer 3, in the case of measuring the A group elements in the oxide film layer 3, the thickness of the oxide film layer 3 and t, oxide film layer 3 It detected intensity of the a group element in a range of the maximum value of the detected intensity of the a group element a, up to 2t / 3 ~ t in the thickness direction from the surface of the oxide film layer 3 on the surface-thickness direction in the range up to t / 3 of When the average value and b, a is in the 3.0 times or more of b (a / b ≧ 3.0) . Ie, A group element is concentrated in the surface portion of the oxide film layer 3. Preferably, an a / b ≧ 8.0, more preferably a / b ≧ 10.0. The upper limit of a / b is not particularly defined, but if considering the hot stamping conditions, substantially of the order of 50.0.
　Further, it is preferable that the A group element is concentrated more on the surface layer, the maximum value of the detected intensity of the A group element in a range of up to t / 5 on the surface - the thickness direction of the oxide film layer 3 a ', oxide layer When the third surface to the average value of the detected intensity of the a group element and b in the range of the thickness direction to 2t / 3t ~ t, a 'is b 3.0 times or more (a' / b ≧ 3.0) it is preferable that.
　However, if it contains more than one type of A group element of the oxide film layer 3, in many group A elements most content, a / b (preferably a '/ b also) it is satisfies the range described above Bayoi.
　The hot stamp member according to the present embodiment, A group element has largely concentrated on the surface of the oxide film layer 3 as shown in Figure 7A, for example. On the other hand, when not specifically controlled, as shown in FIG. 7B, A group element is not sufficiently concentrated to the surface of the oxide film layer 3.
[0038]
　As described above, in terms of paint adhesion, the thickness of the oxide film layer 3 is preferably from 0.01 ~ 10.0 [mu] m. However, thickening of the A group element is simultaneous with the formation of the oxide film layer 3. Thin oxide film layer 3, i.e., the short time that the oxide film layer 3 is formed, also enrichment of the surface layer portion of the A group element becomes insufficient. Therefore, the oxide film layer 3, if to enrich A group element in the surface portion, the thickness of the oxide film layer 3 is preferably not less than 0.10 .mu.m. That is, when improving the paint adhesion and pitting corrosion resistance, it is preferable that the thickness of the oxide film layer 3 and 0.10 ~ 10.0 [mu] m.
[0039]
(Steel 1)
　Next, the steel 1 having the hot stamp member according to the present embodiment is not particularly limited as long as it is suitably available steel hot stamping. For example a possible steel applied to hot stamp member according to the present embodiment, the chemical components are mass%, C: 0.1 ~ 0.4% , Si: 0.01 ~ 0.60%, Mn: 0.50 ~ 3.00%, P: 0.05% or less, S: 0.020% or less, Al: 0.10% or less, Ti: 0.01 ~ 0.10%, B: 0.0001 ~ 0.0100 %, N: containing 0.010% or less, can be exemplified steel balance being Fe and impurities. The form of the steel product 1 can be exemplified steel such as hot-rolled steel sheets and cold-rolled steel sheet, for example. The following describes components of the steel material.
[0040]
C: 0.1 ~ 0.4%
　C is contained in order to ensure the mechanical strength of interest. When C content is less than 0.1%, not obtained sufficient improvement of mechanical strength, the effect of containing C becomes poor. On the other hand, if the C content exceeds 0.4%, although it is possible to further cure improve the strength of the steel sheet, the elongation, the diaphragm tends to decrease. Therefore, C content is preferably in the range of 0.4% or less than 0.1% in mass%.
[0041]
Si: 0.01 ~ 0.60% Si
　is one of the strength improving elements to improve mechanical strength, is included to ensure mechanical strength to the same manner as C purposes. When Si content is less than 0.01%, hardly exhibits the strength improving effect is not sufficient improvement in mechanical strength can be obtained. Meanwhile, Si, when the Si content because that is also easily oxidizable elements exceeds 0.60 percent due to the effect of Si oxide formed on the steel sheet surface layer, when performing molten Al plating, lowering the wettability and, there is a possibility that the non-plating occurs. Therefore, Si content is preferably in the range of 0.60% 0.01% in mass%.
[0042]
Mn: 0.50 ~
　3.00% Mn is one of the strengthening element to strengthen the steel, is also one of the elements to improve the hardenability. Furthermore Mn may also be effective in preventing hot embrittlement due to S which is one of the impurities. When Mn content is less than 0.50%, these effects can not be obtained, the effect is exhibited at 0.50% or more. Meanwhile, Mn is because an austenite forming element, when the Mn content exceeds 3.00%, there is a possibility that the strength too much residual austenite phase is reduced. Therefore, Mn content is preferably in the range of less 3.00% 0.50% or more by mass%.
[0043]
P: 0.05% or less
　P is an impurity contained in steel. P contained in the steel material may be segregated in the grain boundary of the steel material lowers the toughness of the base material of the hot stamped shaped body, reducing the delayed fracture resistance of the steel. Therefore, the P content of steel is preferably 0.05% or less, the content of P is preferably as small as possible.
[0044]
S: 0.020% or less
　S is an impurity contained in steel. S contained in the steel reduces the toughness of the steel material to form a sulfide, it may decrease the resistance to delayed fracture of the steel. Therefore, S content of the steel is preferably 0.020% or less, S content of the steel is preferably as small as possible.
[0045]
Al: 0.10% or less
　Al is generally used in the deoxidation purposes of steel. However, if the Al content is high, Ac steel 3 for points is increased, it is necessary to raise the heating temperature required for hardening ensuring the steel during hot stamping, on a hot stamp manufacturing is undesirable. Therefore, Al content of the steel is preferably 0.10% or less, more preferably 0.05% or less, still more preferably 0.01% or less.
[0046]
Ti: 0.01 ~
0.10% Ti is one of the reinforcement elements. When Ti is less than 0.01% is not obtained, the strength improving effect and oxidation resistance improving effect, these effects are exhibited at least 0.01%. Meanwhile, Ti is too is too contained, for example, by forming a carbide or nitride, it is a steel may be softened. Particularly, when the Ti content exceeds 0.10% is likely not yield mechanical strength of interest. Therefore, Ti content is preferably in the range of 0.10% 0.01% in mass%.
[0047]
B: 0.0001 ~ 0.0100%
　B has the effect of improving the strength by acting upon quenching. When B content is less than 0.0001%, the lower such strength improving effect. On the other hand, if the B content exceeds 0.0100%, the inclusions are formed by steel embrittlement, fatigue strength may be reduced. Therefore, B content is preferably in the range of 0.0100% 0.0001% or more by mass%.
[0048]
N: 0.010% or less
　N is an impurity contained in steel. N contained in the steel material may form a nitride lowers the toughness of the steel. Further, N included in the steel material, when B is contained in steel, B binding to reduce solid solute B amount and, in some cases reduce the hardenability improving effect of B. Therefore, N content of the steel is preferably 0.010% or less, N content of the steel is more preferably as small as possible.
[0049]
　Further, the steel material constituting the hot stamp member according to the present embodiment may also include further Cr, an element for improving the hardenability such as Mo.
[0050]
　Cr:
　0 ~ 1.0% Mo: 0 ~ 1.0%
　for improving the hardenability of the steel, Cr, may contain one or both of Mo. In order to obtain this effect, both the content is preferably set to 0.01% or more. On the other hand, the effect of the content as 1.0% or more on the saturation, cost increases. Therefore, it is preferable that the content be 1.0% or less.
[0051]
　Balance other than the components being iron and impurities. The steel may contain impurities that would be incorporated in such other manufacturing processes. As the impurity, for example, B (boron), C (carbon), N (nitrogen), S (sulfur), Zn (zinc), Co (cobalt) and the like.
[0052]
　Steel having the chemical components, the heating and quenching by the hot stamping method, it is possible to hot stamp member having about 1000MPa or more tensile strength. In the hot stamping method, it is possible to perform the press working in a state of softened at high temperature, it can be easily molded.
[0053]
(Production method of hot stamping member)
　Next, an example of a manufacturing method of hot stamping member according to the present embodiment will be described with reference to FIG. Manufacturing method described below is subjected to Al plating steel and aluminum plating steel, by performing hot stamping process on aluminum plating steel, among Al-Fe metal steel material 1 surface compound layer 2 and the oxide film layer 3 is an example of forming a. However, the methods described herein is merely an example and is not particularly limited to this method.
[0054]
　
(immersion in the plating bath)
　to form an Al plating layer on the surface of the steel sheet by, for example, melt plating. Al plating layer of aluminum plating steel is formed on one or both surfaces of the steel.
　In such as during the heating step in the hot-dip plated or during hot stamping, at least a part of Al contained in the Al plating layer may be Fe alloyed in steel. Therefore, the Al plating layer is not necessarily limited to component is formed in a constant single layer may include a layer that is appropriately alloyed.
[0055]
　The hot dipping bath at the hot dipping, is contained Al and A-group element. It may also contain a Si in molten plating bath. A group element to be added to the molten bath by more than 0.001 mass% to 30 mass%, Si is 20 mass% or less. Al, by immersing the steel in a molten plating bath moistened with Si if group A element and necessary, to form an Al plating layer on the surface of the steel material. The Al coating layer formed include A group element. In some cases, including the Si and Fe.
[0056]
(Spraying particles)
　Next, before the relative steel 1 immediately after pulled from the molten coating bath, the molten metal adhering to the steel by immersion into the molten coating bath (plating metal 21 in the molten state) solidifies, nitriding things, carbide, particles 10 such as an oxide air, together with the cooling gas, such as nitrogen or argon blowing. The sprayed particles 10 becomes a nucleus for crystal, the plating metal 22 solidified, the effect of reducing the crystal grain size of the Al plating layer. This effect is particularly large in the surface side of blowing particles. Crystal grain boundary is increased by reducing the grain size of the Al plating layer, followed by the interfacial area between the atmospheric gas atmosphere or the like during hot stamp heated performed increases. For group A element has a high affinity for atmospheric gas increases the amount of concentrated in the surface layer, the proportion of the group A elements in the surface layer of the oxide film layer 3 is increased.
[0057]
　Nitrides blowing, carbides, the size of the particles 10, such as oxide is not particularly limited. However, if the particle diameter exceeds 20 [mu] m, the crystal grains of the Al plating layer is increased, A group element is less likely to concentrated in the surface layer. Therefore, it is desirable that the particles 10 having a particle size of 20μm or less. Nitrides blowing, carbides, oxides, titanium nitride, silicon nitride, titanium carbide, silicon carbide, titanium oxide, silicon oxide, iron oxide, and aluminum oxide. Adhesion amount of the particles 10, for example, 0.01 ~ 1.0 g / m 2 preferably set to. The amount of adhered particles 10 With this range, Al plating layer, a sufficient amount of crystal nuclei are formed in particular surface portion, in the. The crystal grain size in this for Al plating layer is sufficiently small, it is possible to enrich A group element in the surface portion of the oxide film layer 3 by heating during hot stamping.
[0058]

　the aluminum-plated steel which is manufactured in the above, to implement hot stamping. Hot stamping method, after an aluminum-plated steel optionally blanking (punching), it is softened by heating the aluminum plating steel. Then, the softened aluminum-plated steel press working by molding, then cooled. Steel 1 is hardened by heating and cooling, about 1000MPa or more high tensile strength. As the heating method, ordinary electric furnace, in addition to the radiant tube furnace, it is possible to employ an infrared heating or the like.
[0059]
　The heating temperature and the heating time in the hot stamp, it is preferably not less than 2 minutes when 850 ~ 950 ° C. in an air atmosphere. When the heating time is shorter than 2 minutes, for enrichment of the group A elements to oxide film layer 3 in does not proceed, paint adhesion and pitting corrosion resistance improving effect of the hot stamp member becomes insufficient.
　Further, if the oxygen concentration is hot stamped in a 5% or less of the atmosphere, the heating time is preferably 3 minutes or more. For the thickness of the heating time is shorter than 3 minutes oxide film layer 3 is not sufficiently large, and the proportion of the group A elements in the oxide film layer 3, concentrated to group A elements into the surface portion of the oxide film layer 3 It becomes insufficient.
[0060]
　By hot stamping, Al plating layer is changed to Al-Fe intermetallic compound layer 2, also, the surface of the Al-Fe intermetallic compound layer 2 is an oxide film layer 3 is formed. Al plating layer is melted by heating during hot stamping, also by Fe diffuses from the steel material 1, Al-Fe intermetallic compound layer 2 containing Al-Fe alloy phase and Al-Fe-Si alloy phase formed It is. Al-Fe intermetallic compound layer 2 is not necessarily limited to component composition is formed by the constant single layer, it can be assumed to partially contain an alloyed layer.
　Also, concentrates A group element contained in the Al coating layer on the surface layer of the Al plating layer, that the oxygen in the atmosphere the surface of the Al plating layer is oxidized, the oxide film layer 3 including the group A elements It is formed. By performing the particles 10 spraying, Al-plated layer, a sufficient amount of crystal nuclei are formed in particular surface portion, in the. Thus the crystal grain size of the Al plating layer becomes sufficiently small, it is possible to enrich A group element in the surface portion of the oxide film layer 3 by hot stamping heating. The added A-group element in the Al coating layer to the whole may be shifted to the oxide film layer 3, a portion remains in Al-Fe intermetallic compound layer 2, the balance shifts to the oxide film layer 3 it may be.
[0061]
　Instead of hot dipping, by depositing Al and A-group element by vapor deposition or thermal spraying on the surface of the steel material 1, to form an Al coating layer containing a group A element, further, the steel 1 having the Al coating layer the by hot stamping, hot stamping member according to the present embodiment may be manufactured.
　As an example of a method of forming an Al coating layer, by vapor deposition or thermal spraying, previously depositing the Al against steel, then it may be deposited A group element. Thus, Al coating layer made of an Al layer and a A group element is formed.
　Another example of a method of forming an Al coating layer, by performing vapor deposition or thermal spraying using a vapor deposition source or spraying source moistened with A group element, even at the same time adhere to the steel of Al and A-group element good. The proportion of the group A elements in the Al coating layer is preferably 0.001% to 30 mass%.
[0062]
　Thereafter, as in the case of aluminum-plated steel, by performing hot stamping on steel 1 having an Al coating layer can be produced hot stamp member according to the present embodiment.
Example
[0063]
　Although examples of the present invention will be described, the conditions of Example is an example of conditions adopted for confirming the workability and effects of the present invention, the present invention be limited to this single condition example Absent. The present invention does not depart from the gist of the present invention, as long as they achieve the object of the present invention may employ various conditions.
[0064]
　The steel sheet before plating, the steel sheet having high mechanical strength (tensile strength, yield point, elongation, diaphragm, hardness, impact value, means the properties related to mechanical deformation and destruction of such fatigue strength.) The it is desirable to use. Used in hot stamping steel plate of the present invention, an example of the steel sheet before plating shown in Table 1.
[0065]
[Table 1]

[0066]
　To steel sheet having a chemical composition according (steel No.S1 ~ S18) shown in Table 1, to form an Al plating layer on both surfaces of the steel sheet by hot dipping. And plating bath temperature is 700 ° C. at the time of hot dipping, after dipping the steel sheet in a plating bath, the coating weight per one side 70 g / m by a gas wiping method 2 was adjusted to. Then, for example, excluding the sign a4, a5, before the plating layer solidifies, the average coating weight of 0.1 g / m 2 was sprayed titanium oxide having a particle size of 0.05μm so as to. The sign a4, a5, was not sprayed particles.
　The plating bath is contained below 30.0% 0.001% or more of group A element in mass%. The group A element selected Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Mg, Ca, Ba, Sr, one or more of Ti. Was then heated Al-plated steel sheet in an electric resistance furnace at a furnace temperature 900 ° C. As the soaking time is between 5 minutes. Then cooled in the mold and simultaneously molded in a mold to obtain a hot stamp member.
[0067]
　The resulting hot stamp member, the ratio of group A element in an oxide film layer of the hot stamping member, thickening degree of the A group element in the surface of the oxide film layer of the hot stamping member, compounds contained in the oxide film layer, an oxide film to investigate the thickness of the layer. Further, as the properties were investigated paint adhesion, corrosion resistance after coating, and pitting corrosion resistance. Results Table 2A, shown in Table 2B.
　Not shown in the table, in each of the examples, the thickness of the Al-Fe intermetallic compound layer was in the range of 0.1 ~ 10.0 [mu] m.
[0068]
(1) oxide layer
　compound species of the oxide layer was determined by measuring the electron beam diffraction using a TEM (transmission electron microscope). The ratio of the element A was measured using EDX (energy dispersive X-ray spectroscopy) function of TEM (transmission electron microscope). The EDX features, among the constituent elements of the oxide film layer, determined the content of the constituent elements except for oxygen, respectively, by obtaining the sum of the content of the group A elements of which, except for the oxygen in the oxide film layer A It was determined the presence proportion of the group elements. Specifically, it determined group A elements, Al, the existence ratio of the group A elements when the total amount of Si and Fe is 100 atomic% by atomic%.
　Oxide layer of this obtained in Examples and Comparative Examples, contains an oxide of the group A elements, including aluminum oxide in the other remainder was further contain impurities. Furthermore Test Examples contained a silicon oxide.
　The thickness of the oxide layer was determined it is determined that the interface of the position where the detection intensity of oxygen was decreased to 1/6 of the maximum value by using a GDS oxide film layer and the Al-Fe intermetallic compound layer. More specifically, when the oxygen measured in the sputtering rate from the surface by 0.1 seconds in the thickness direction of the 0.060Myuemu / sec oxide layer in GDS, the detection intensity of oxygen atoms is equal to the maximum value 1/6 of become measurement time, the longest time is T [sec], by multiplying the sputtering rate to T, was determined the thickness of the oxide film layer.
[0069]
　Also, for the most often A group element of content, the maximum value of the detected intensity of the A group element in a range of 1/3 times the position of the oxide film thickness in the thickness in the thickness direction from the surface-surface (measuring time 0 ~ T / 3 the maximum value of the detected intensity of the a group element in seconds), the surface layer from the interface between the two thirds of the position and the oxide film layer of the oxide film thickness in the thickness in the thickness direction and Al-Fe intermetallic compound layer the average value of the detected intensity of the a group element in the range (average value of the detected intensity of the a group element in the measurement time T / 3 (sec.) ~ T (sec)) was determined ratio (Table in detection intensity ratio 1 ).
　Similarly, the maximum value of the detected intensity of the A group element in a range of 1/5 times the position of the oxide film thickness in the thickness in the thickness direction from the surface-surface, the oxide film thickness in the thickness direction from the surface layer of thickness 2/3 times and locations - oxide film layer and the Al-Fe intermetallic compound layer and the average value of the detected intensity of the a group element in the region of the interface, were also determined ratio (Table in the detection intensity ratio 2).
[0070]
(2) Paint adherence
　coating adhesion was evaluated according to the method described in Japanese Patent No. 4373778. That is, 100 cutting a cross-cut of 1mm intervals with a cutter after immersion for 240 hours the sample in deionized water 60 ° C., based on the calculated area ratio by measuring visually the number of peeled portions of the cross-cut portion It was scored.
(Score)
3: Peeling area is 0% or higher less than 10%
less than 2: Peeling area of 10% or more 70%
1: 100% less than 70% peeling area
[0071]
(3) corrosion resistance after painting
　corrosion resistance evaluation after the painting was carried out by the method specified in the Society of Automotive Engineers enactment of JASO M609. Put flaw with a cutter in the coating film, the width of blistering the coating film from the cut flaw after the corrosion test 180 cycles (one maximum value) was measured.
(Evaluation)
3: less than blister width 0mm or 1.5mm
2: less than blister width 1.5mm or 3mm
1: blister width 3mm or more
[0072]
(4) the pitting corrosion resistance
　evaluation of pitting corrosion resistance was performed by the following method.
　After the sample was immersed for 1 minute at room temperature to Nippon Parkerizing Co. surface modifier Prepalene X, it was immersed for 2 minutes at 35 ° the company painted undercoat chemical treating agent PALBOND SX35. Then subjected to combined cycle corrosion test in accordance with the method described in JIS H 8502. Japan coating film having a thickness of 15μm was applied with a paint manufactured by power float 1200 was granted cut with a cutter knife, as described in JIS H 8502. From a thickness reduction of the steel sheet after 60 cycles elapse of the portion imparted with cut and scored as follows.
[Score]
5: sheet thickness reduction 0.1mm less than
4: thickness reduction amount 0.1mm or 0.2mm less than
3: thickness reduction amount 0.2mm or 0.3mm less than
2: thickness reduction amount 0.3mm or 0.4mm less than
1: plate thickness reduction 0.4mm or more
[0073]
[Table. 2A]

[0074]
[Table 2B]

[0075]
　As in the invention examples A1 ~ A57, the inclusion in a ratio within the range of the invention the group A elements in the oxide film layer, excellent paint adhesion. As a result, the corrosion resistance after painting, was excellent. Further, in the invention Examples A1 ~ A57, A group element had concentrated in the surface portion of the oxide film layer. For this reason, and also excellent in the pitting corrosion resistance.
　In contrast, Comparative Examples not containing the A group element in the oxide film layer a1, the thickness of the outer percentage invention range A group element in the oxide layer and / or the oxide film layer is outside the invention range a2 , a3, a6, a7, a8, a9 was inferior to the paint adhesion and / or pitting corrosion resistance. Further, a4, a5, so was not sprayed particles, A group element is not concentrated in the surface portion of the oxide film layer, pitting corrosion resistance was poor.
[0076]
[table 3]

[0077]
　Further, Invention Examples B1 ~ B7 shown in Table 3, the Si content of the plating bath by 8% or more, was controlled so as to contain Si in Al-Fe intermetallic compound.
　As can be seen from the results in Table 3, Inventive Examples B1 ~ B7 is excellent in corrosion resistance after painting as compared with the invention examples A27 containing little Si to Al-Fe intermetallic compound layer. This Si oxide produced in the time of the corrosion test is excellent in water resistance is believed to be because the effect of suppressing corrosion. In any of the examples of B1 ~ B7, the thickness of the Al-Fe intermetallic compound layer was in the range of 0.1 ~ 10.0 [mu] m.
[0078]
　Having described in detail preferred embodiments of the present invention, it goes without saying that the present invention is not limited to such an example. It would be appreciated by those skilled in the relevant field of technology of the present invention, within the scope of the technical idea described in the claims, it is intended to cover various changes and modifications also should be understood that such modifications and changes belong to the technical scope of the present invention for these.
Industrial Applicability
[0079]
　The present invention can provide an excellent hot stamp member adhesion (coating adherence) and pitting corrosion resistance of the electrodeposition coating film. Therefore, there is a high availability of the industry.
DESCRIPTION OF SYMBOLS
[0080]
　1 steel
　2 Al-Fe intermetallic compound layer
　3 oxide film layer
　10 particles
　21 plated metal (molten
　state) 22 plated metal (solidified state)

The scope of the claims

[Requested item 1]And steel,
　said a steel Al-Fe intermetallic compounds formed on the layer,
　anda oxide film layer formed on the Al-Fe intermetallic compound layer,
　the oxide layer is, Be, Mg , Ca, Sr, Ba, Sc , Ti, V, Cr, Mn, Fe, Co, Ni, Cu, and one or more group a element selected from the group consisting of Zn, and Al, and oxygen consists impurity,
　the ratio of the group a elements excluding the oxygen of the oxide film layer is 0.01 atomic% or more and 80 atomic% or less,
　the oxide film layer thickness t of 0.1 to 10 a .0Myuemu,
　using GDS, the thickness direction from the surface of the oxide film layer, when measured with a group element of the oxide layer in the range from the surface to 1/3 of the thickness t range maximum value of detected intensity of the a group element is from 2/3 of the thickness t to t in The average value of the detected intensity of definitive the A group element is 3.0 times or more,
hot stamping member.
[Requested item 2]
　The maximum value of the detected intensity of the A group element is, the average value of the detected intensity of the A group element is 8.0 times or more,
hot stamp member according to claim 1.
[Requested item 3]
　Component of the steel product, by
　mass%,
　C: 0.1
　~ 0.4%, Si: 0.01 ~ 0.60%, Mn: 0.50 ~
　3.00%, P: 0.05% or less ,
　S: 0.020% or
　less, Al: 0.10% or
　less,
　Ti: 0.01 ~ 0.10%, B: 0.0001 ~
　0.0100%, N: 0.010% or less,
　Cr: 0
　1.0% ~, Mo: 0 ~ 1.0%,
　wherein the balance being Fe and impurities,
hot stamp member according to claim 1 or 2.
[Requested item 4]
　The components of the steel material, in mass%, Cr: 0.01 ~ 1.0%, Mo: including either or both of from 0.01 to 1.0% hot stamp member according to claim 3.
[Requested item 5]
　The Al-Fe intermetallic compound layer containing Si, hot stamp member according to any one of claims 1 to 4.