JP5230318B2 - Plated steel material having high corrosion resistance and excellent workability, and manufacturing method thereof - Google Patents

Description

  The present invention relates to a plated steel material having high corrosion resistance, and more specifically, after processing, it can be applied mainly for various uses outdoors, for example, for piping, building materials, civil engineering, agriculture, and fishery. The present invention relates to a hot dipped steel material and a manufacturing method thereof.

  Steel materials used outdoors are used after being hot dip galvanized for the purpose of imparting corrosion resistance. Since the corrosion resistance is better as the adhesion amount of galvanization is larger, in steel materials that require high corrosion resistance, it is common to increase the adhesion amount by increasing the immersion time.

  However, if the immersion time is excessively long, the Fe—Zn alloy layer develops, resulting in poor appearance called “yake”, lowering workability, and easy peeling of the plating. There is a limit to improving the corrosion resistance by increasing the amount of adhesion.

  Therefore, a two-step plating method has been proposed in which galvanized steel is further plated with good corrosion resistance. For example, Patent Literature 1 discloses a plating method in which hot dip galvanization is performed on a steel material surface and then hot dip Zn-Al alloy plating is performed. Patent Document 2 discloses a plating method in which hot dip galvanization is performed on a steel material surface and then hot dip Zn-Al-Mg alloy plating is performed.

  In addition to the method of plating on such steel materials, Patent Document 3 discloses a method of obtaining a target steel material by processing and welding a steel plate on which high corrosion resistance plating has been performed in advance.

  In recent years, the use of plated steel pipes for piping has increased as one of such plated steel materials. As for plated steel pipes for piping, mechanical joints are becoming widespread from the viewpoint of strict and diversified required quality of joints, and are used after being subjected to flare processing or the like. Flare processing is a strict process that widens the end of the tube to an angle of about 90 °, so that plating peeling easily occurs during processing.

JP-A-52-30233 JP 2002-47549 A JP 2002-115793 A

  The demand for improvement in corrosion resistance tends to increase further, and the conventional hot dip galvanizing and the two-step plating on which hot dip Zn-Al alloy plating is applied have insufficient corrosion resistance and sufficiently satisfy the demands of customers. I can't do that.

  Further, the molten Zn—Al—Mg alloy-plated steel material disclosed in Patent Document 2 does not have sufficient plating adhesion during processing, and plating peeling occurs during flare processing. Furthermore, the hot-dip Zn-Al-Mg alloy-plated steel pipe disclosed in Patent Document 3 has a problem in that the welded part is not plated during welding, so that the welded part needs to be repaired by thermal spraying or the like, resulting in an increase in production cost. is there.

  Therefore, in view of the above-described present situation, the present invention aims to provide a hot-dip galvanized steel material having high corrosion resistance and excellent workability, and a method for producing the same.

  As a result of intensive research on high corrosion resistance hot dip galvanized steel materials, the present inventors have conducted a hot dip galvanization on the steel material surface, followed by hot dip galvanization, followed by hot dip galvanization steel plating. By optimizing the structure, it has been found that a hot-dip galvanized steel material having high corrosion resistance and excellent plating adhesion during processing can be produced, and the present invention has been made.

  That is, the gist of the present invention is as follows.

( 1 ) In mass%,
C: 0.005 to 0.15%,
Si: 0.15-0.25%,
Mn: 0.40 to 1.6%
P: 0.04% or less,
S: 0.04% or less,
Al: 0.001 to 0.06%,
N: 0.0080% or less,
On the surface of the steel material composed of the remaining Fe and unavoidable impurities , an Fe—Al—Zn—Si alloy layer is provided as a lower layer, and an intermediate layer is further provided with an intermediate layer of mass%, Al: 4 to 20%, Fe: 0 0.1 to 15%, Mg: 0.1 to 5%, the balance having an alloy layer made of Zn and inevitable impurities, and further, as an upper layer, by mass%, Al: 4 to 20%, A plated steel material having high corrosion resistance and excellent workability, characterized by having an alloy layer composed of Mg: 0.1 to 5% and the balance being Zn and inevitable impurities.
( 2 ) In the plated steel material having high corrosion resistance and excellent workability as described in ( 1) above, the plated steel material having high corrosion resistance and excellent workability characterized by containing Mg in the lower alloy layer .

( 3 ) In the plated steel material having high corrosion resistance and excellent workability as described in either (1) or (2) above, in the intermediate layer, or any of the alloy layers of the intermediate layer and the upper layer A plated steel material having high corrosion resistance and excellent workability, characterized by containing 0.0005 to 0.8% of Si.

( 4 ) In the plated steel material having high corrosion resistance and excellent workability according to any one of (1) to ( 3 ), the thickness of the intermediate layer is at least twice the thickness of the upper layer. Plated steel with high corrosion resistance and excellent workability.

( 5 ) In the plated steel material having high corrosion resistance and excellent workability as described in ( 4 ) above, the difference between the maximum value and the minimum value of the thickness of the intermediate layer is within 30 μm. A plated steel material with excellent workability.

( 6 ) The plated steel material having high corrosion resistance and excellent workability, wherein the plated steel material having high corrosion resistance and excellent workability according to any one of (1) to ( 5 ) is a steel pipe .

( 7 ) In the two-stage plating method in which hot dip galvanizing is performed on the surface of the steel material and then hot dip galvanizing is performed, as the first step, dip galvanizing is performed by immersing in a plating bath mainly composed of zinc. In addition, as a second stage, a hot-dip zinc alloy plating is performed by immersing in either a molten Zn-Al-Mg plating bath or a molten Zn-Al-Mg-Si plating bath. Method.

( 8 ) In the method for producing a plated steel material according to ( 7 ), the hot dip galvanizing bath as a first stage is mass%, Zn: 99% or more, and the balance is an inevitable impurity. A method for producing a plated steel material.

( 9 ) In the method for producing a plated steel material according to ( 7 ), the hot dip galvanizing bath as the first stage is in mass%, Al: 0.001 to 0.5%, and Ni: 0.001. A method for producing a plated steel material, comprising one or two of ~ 0.2%, the balance being Zn and inevitable impurities.

( 10 ) In the method for producing a plated steel material according to any one of ( 7) to ( 9 ), the molten Zn—Al—Mg plating bath as the second stage is in mass%, Al: 4 to 20%, A method for producing a plated steel material, containing Mg: 0.1 to 5%, with the balance being Zn and inevitable impurities.

( 11 ) In the method for producing a plated steel material according to any one of ( 7 ) to ( 9 ), the molten Zn—Al—Mg—Si plating bath as the second stage is in mass%, and Al: 4 to 20 %, Mg: 0.1 to 5%, Si: 0.0005 to 0.8%, the balance being Zn and inevitable impurities, a method for producing a plated steel material

( 12 ) In the method for producing a plated steel material according to any one of claims 7 to 11 , in the first stage plating step, an object to be plated is a hot dip galvanizing bath at a temperature of 430 to 500 ° C for 100 seconds. After performing immersion plating by dipping as described above, the object to be plated is subjected to a molten Zn—Al—Mg plating bath at a temperature of 400 to 480 ° C. or a molten Zn—Al—Mg—Si plating in the second plating step. A method for producing a plated steel material, characterized by performing hot dip zinc alloy plating by immersing in a bath for 30 seconds or more.
( 13 ) In the method for producing a plated steel material according to ( 12 ), the object to be plated that has been hot-plated in the first-stage plating step is melted in the second-stage plating step while maintaining the temperature at 300 ° C. or higher. A method for producing a plated steel material, characterized by performing plating.

( 14 ) In the method for producing a plated steel material according to any one of ( 7 ) to ( 13 ), as a pretreatment, an object to be plated is treated with a ferric chloride solution. .

  The present invention has a high corrosion resistance by optimizing the structure of the plating layer in a two-stage plating method in which hot dip galvanization is performed on the steel surface and then hot dip galvanizing is performed. This makes it possible to provide a hot dip galvanized steel material having excellent plating adhesion, and contributes greatly to the development of the industry.

  The present invention is described in detail below.

  The hot dip galvanized steel material of the present invention has a Fe-Al alloy layer, an Fe-Al-Zn alloy layer, an Fe-Al-Si alloy layer, an Fe-Al-Zn-Si alloy layer, and a lower layer on the surface of the steel material. In addition, any one of these alloy layers containing Mg is included in these alloy layers, and on that, as an intermediate layer, by mass%, Al: 4-20%, Fe: 0.1-15 %, Mg: 0.1 to 5%, the balance being an alloy layer made of Zn and inevitable impurities, and further, as an upper layer, mass%, Al: 4 to 20%, Mg: 0.00. It is a hot dip galvanized steel material having an alloy layer of 1 to 5%, the balance being Zn and inevitable impurities.

  In the present invention, the plated steel material is a steel material provided with a zinc-based plating layer. As the base steel material of the present invention, both hot-rolled steel material and cold-rolled steel material can be used, and the steel types are Al killed steel, Si killed steel, ultra low carbon steel added with Ti, Nb, etc., and P, Si Various materials such as high-strength steel and stainless steel to which reinforcing elements such as Mn are added can be applied.

  Various shapes such as a wire shape such as a steel wire, a plate shape such as a steel plate, a net shape, a cylindrical shape such as a steel pipe, and a three-dimensional shape such as a rod shape can be used as the shape of the plated steel material. For example, from small base materials such as bolts, nuts and power transmission brackets to large base materials such as railings, main pillars, guard fences for bridges, road signs, road card fences, river fences, rockfall prevention nets, steel pipes, etc. it can.

  The lower alloy layer includes an Fe—Al alloy layer, an Fe—Al—Zn alloy layer, an Fe—Al—Si alloy layer, an Fe—Al—Zn—Si alloy layer, and Mg contained in these alloy layers. Any one of the alloy layers. These alloy layers are the same as the alloy layers called the Fe-Al alloy layer or the Fe-Al-Zn alloy layer observed at the plating / steel interface of the hot dip galvanized steel sheet produced in the continuous galvanized steel sheet line. Is.

This alloy layer is an alloy mainly composed of Fe ₂ Al ₅ or FeAl ₃ , but a part of Al is substituted with Zn, and Fe ₂ (Al _1-x , Zn _x ) ₅ or Fe ( al _1-x, also reported that there as Zn _{x) 3} is.

  Further, when Si is present in the steel or the plating bath, a part of Al is further replaced with Si, and is observed as an Fe—Al—Si alloy layer or an Fe—Al—Zn—Si alloy layer. . Further, when Mg is present in the plating bath, Mg may be further observed in the alloy layer.

  Any alloy layer is easily observed as an Al-concentrated layer when observed from the cross section with EPMA. Since the alloy layer is thin, it is difficult to determine the composition from EPMA, but the Al-enriched layer observed at the plating / steel interface is an Fe-Al alloy layer or Fe-Al- A layer in which concentration of Si is confirmed is referred to as a Zn alloy layer, and a layer in which Si concentration is confirmed is referred to as an Fe—Al—Si alloy layer or an Fe—Al—Zn—Si alloy layer. Although the thickness is not particularly specified, the thickness observed by the present inventors was 0.5 to 5 μm.

  When any one of the Fe-Al alloy layer, Fe-Al-Zn alloy layer, Fe-Al-Si alloy layer, and Fe-Al-Zn-Si alloy layer is present, these layers are made of steel. Since this works as a barrier layer that inhibits the diffusion of Fe and prevents the formation of a brittle Fe—Zn alloy layer, this Fe—Al alloy layer, Fe—Al— It is necessary to form any one of a Zn alloy layer, an Fe—Al—Si alloy layer, and an Fe—Al—Zn—Si alloy layer.

  Next, the hot-dip galvanized steel material of the present invention is, on the lower layer, as an intermediate layer, in mass%, Al: 4-20%, Fe: 0.1-15%, Mg: 0.1-5% The balance has an alloy layer made of Zn and inevitable impurities. Hereinafter, “%” means mass%.

  The reason why the content of Al is limited to 4 to 20% is that if the content is less than 4%, the effect of improving the corrosion resistance is insufficient, and if the content exceeds 20%, the effect of improving the corrosion resistance is saturated. is there. Further, Al needs to be added in an amount of 4% or more in order to prevent oxidation of Mg in the plating bath.

  The reason why the content of Fe is limited to 0.1 to 15% is that if it is less than 0.1%, the effect of improving the plating adhesion is insufficient, and if it exceeds 15%, the plating adhesion is reduced. This is because the improvement effect is saturated.

The molten Zn—Al—Mg plating has a ternary eutectic structure of Zn / Al / MgZn ₂ , and the MgZn ₂ phase in the eutectic structure is hard and brittle, which causes plating peeling during processing. On the other hand, when Fe is added to this, each phase is refined and a lamellar ternary eutectic structure is not formed.

Since the phases identified by X-ray diffraction are Zn phase, Al phase, and MgZn ₂ phase, it is considered that the basic phase structure has not changed, but as long as it is observed with an optical microscope and SEM from the cross section. A clear ternary eutectic structure is not observed, but is observed as a collection of fine solidified structures.

Therefore, the addition of Fe, MgZn ₂ phase, because it will not be formed in layers, it is possible to prevent the plating peeling due to the MgZn ₂ Aichu crack propagates.

  In order to increase the amount of adhesion for the purpose of improving the corrosion resistance in the two-step plating, in the first-step plating, the immersion time is lengthened and the Fe—Zn alloy layer is appropriately developed, as described later. Therefore, it is necessary to effectively use this Fe—Zn alloy layer. Therefore, in order to increase the adhesion amount for the purpose of improving the corrosion resistance, it is necessary to contain Fe in the plating layer.

  The reason why the Mg content is limited to 0.1 to 5% is that if it is less than 0.1%, the effect of improving the corrosion resistance is insufficient, and if it exceeds 5%, the plating layer becomes brittle. This is because the adhesion decreases.

Mg contributes to improving corrosion resistance by being finely dispersed in the plating layer as an MgZn ₂ phase. Since Mg promotes the formation of ZnCl ₂ · 4Zn (OH) ₂ , the zinc corrosion product during corrosion becomes a protective film by finely dispersing the MgZn ₂ phase in the plating layer. It becomes possible to improve.

  Furthermore, the hot dip galvanized steel material of the present invention is an alloy composed of Al: 4 to 20%, Mg: 0.1 to 5%, and the balance of Zn and inevitable impurities as an upper layer on the intermediate layer. Has a layer.

  The reason why the content of Al is limited to 4 to 20% is that if the content is less than 4%, the effect of improving the corrosion resistance is insufficient, and if the content exceeds 20%, the effect of improving the corrosion resistance is saturated. is there. Further, Al needs to be added in an amount of 4% or more in order to prevent oxidation of Mg in the plating bath.

  The reason why the content of Mg is limited to 0.1 to 5% is that if it is less than 0.1%, the effect of improving the corrosion resistance is insufficient. If it exceeds 5%, the plating layer becomes brittle, This is because the adhesion decreases.

Mg contributes to the improvement of corrosion resistance by being finely dispersed in the plating layer as the MgZn ₂ phase. Since Mg promotes the generation of ZnCl ₂ · 4Zn (OH) ₂ , the zinc corrosion product during corrosion becomes a protective film by finely dispersing the MgZn ₂ phase in the plating layer, Corrosion resistance can be improved.

Since the upper plating layer has an Fe content of less than 0.1% as an unavoidable impurity, the solidification structure is a ternary eutectic of Zn phase, Al phase, MgZn ₂ phase, Zn / Al / MgZn _2. A metal structure including any one or more of the structures is formed. Therefore, by observing from the cross section, it can be easily distinguished from the lower layer containing Fe.

  Further, for the purpose of improving the corrosion resistance, 0.0005 to 0.8% of Si can be added to the intermediate layer or any one of the intermediate layer and the upper plating layer. The reason why the content of Si is limited to 0.0005 to 0.8% is that if it is less than 0.0005%, the effect of improving the corrosion resistance is insufficient, and if it exceeds 0.8%, the corrosion resistance is reduced. This is because the improvement effect is saturated.

Since Si also promotes the formation of ZnCl ₂ · 4Zn (OH) ₂ , by dispersing Si in the plating layer, the corrosion product of zinc during corrosion becomes a protective film, and corrosion resistance can be improved. It becomes. Si is dissolved in the plating layer in a small amount and is not observed as a single phase, but may be observed as a Si phase or Mg ₂ Si phase when added in a large amount.

  In addition to these, Sb, Pb, Bi, Ca, Be, Ti, Cu, Co, Cr, Mn, P, B, Sn, Zr, Hf, Sr, V, Sc, and REM are used alone in the plating layer. Alternatively, even if it is composite and contained within 0.5%, the effect of the present invention is not impaired, and depending on the amount, it may be preferable in that the appearance is further improved.

In the present invention, for the purpose of obtaining a plating layer having high corrosion resistance and excellent workability, it is desirable to add Mg to the plating layer and to reduce the lamellar MgZn ₂ phase in the plating layer as much as possible.

For this purpose, it is desirable to reduce the Zn / Al / MgZn ₂ ternary eutectic structure in the upper plating layer to 50% or less. Further, it is preferably 10% or less, and if possible, it is desirable not to generate a ternary eutectic structure of Zn / Al / MgZn ₂ .

Alternatively, by reducing the thickness of the upper plating layer as much as possible and using the intermediate layer as a main plating layer, it is possible to prevent plating peeling due to crack propagation in the hard and brittle MgZn ₂ phase. .

  In particular, it is desirable that the thickness of the intermediate layer is twice or more the thickness of the upper layer in order to prevent plating peeling in a severely processed part such as flare processing. Furthermore, desirably, the ratio of both plating layers is three times or more.

  The manufacturing method of the product of the present invention is not particularly limited, and a known hot dip galvanizing method can be applied. Further, the steel material to be plated may usually be subjected to a conventional pretreatment prior to hot dip galvanization, for example, after a surface treatment such as a degreasing treatment, a shot blasting treatment, and an acid cleaning treatment, followed by a flux treatment. May be performed. Furthermore, if necessary, the steel to be plated may be subjected to Ni pre-plating.

  Moreover, if the etching process using a ferric chloride solution is performed before hot dip galvanizing, the thickness of the plating becomes uniform. Therefore, it is desirable to perform the etching process using a ferric chloride solution as a pretreatment.

  The etching treatment with a ferric chloride solution is highly effective when performed after pickling or after shot blasting. After the etching treatment with the ferric chloride solution, flux treatment, pickling or flux treatment is performed, and hot dip galvanization is performed.

  The conditions for the treatment with the ferric chloride solution are not particularly limited, but the material to be plated is placed in a bath in which a 10% to 60% ferric chloride aqueous solution is maintained at 10 to 70 ° C. It is preferable to immerse for 600 seconds.

  In the case of obtaining the plated steel material of the present invention by the two-stage plating method, in order to make the growth of the plating alloy appropriate, as the first stage, hot dip galvanization mainly composed of zinc is performed, and as the second stage, A method of performing molten Zn—Al—Mg plating or molten Zn—Al—Mg—Si plating is desirable.

  The hot dip galvanizing performed in the first stage uses a hot dip galvanizing bath mainly composed of zinc. As the hot dip galvanizing bath, a high purity galvanizing bath or a hot dip galvanizing bath containing 5% by mass or less of one or more metals of Pb, Sb, Bi, and Sn can be used. is there.

  Moreover, when 1 type or 2 types of Al: 0.001-0.5% and Ni: 0.001-0.2% are added by mass%, plating wettability will improve and non-plating etc. Defects can be prevented. Further, in addition to these, Fe, Mg, Si, Ca, Be, Ti, Cu, Co, Cr, Mn, P, B, Zr, alone or in combination, are contained as unavoidable impurities in an amount of less than 0.1% by mass. However, there is no problem because the plating property is not affected. Desirably, a high-purity galvanizing bath of Zn: 99% or more by mass% is used.

The purpose of the hot dip galvanizing performed in the first stage is to appropriately develop the Fe—Zn alloy layer and ensure a sufficient amount of plating. Therefore, it is desirable to perform the first stage hot dip galvanization at a bath temperature of 430 to 500 ° C. and an immersion time of 100 seconds or more. Although there is no particular restriction on the amount of adhesion of the first stage hot dip galvanizing, the amount of adhesion of plating is preferably 100 to 2000 g / m ² from the viewpoint of corrosion resistance after the second stage plating. In particular, when high corrosion resistance is required, it is preferably 300 to 2000 g / m ² .

  For the hot dip galvanization performed in the second stage, a hot dip Zn—Al—Mg plating bath or a hot dip Zn—Al—Mg—Si plating bath is used. As long as the target plating layer is obtained, the content of Al, Mg, and Si is not limited, but Al: 4 to 20%, Mg: 0.1 to 5%, with the balance being Zn and A plating bath containing inevitable impurities or a plating bath containing Al: 4 to 20%, Mg: 0.1 to 5%, Si: 0.0005 to 0.8%, the balance being Zn and inevitable impurities It is desirable to use it.

  The plating bath contains Fe, Ca, Be, Ti, Cu, Ni, Co, Cr, Mn, P, B, and Zr as unavoidable impurities, alone or in combination, and less than 0.1% by mass. However, there is no problem because the plating property is not affected.

  The purpose of hot dip galvanization performed in the second stage is to ensure plating adhesion while ensuring corrosion resistance.

  For this purpose, as a lower layer, Fe—Al alloy layer, Fe—Al—Zn alloy layer, Fe—Al—Si alloy layer, Fe—Al—Zn—Si alloy layer, and Mg in these alloy layers are used. It has any one of the alloy layers to be contained, and on top of that, as an intermediate layer, by mass%, Al: 4-20%, Fe: 0.1-15%, Mg: 0.1-5%, The remaining alloy layer is composed of Zn and inevitable impurities, or by mass: Al: 4-20%, Fe: 0.1-15%, Mg: 0.1-5%, Si: 0.0005-0. 8%, the balance has any of an alloy layer made of Zn and inevitable impurities, and further, as an upper layer, in mass%, Al: 4-20%, Mg: 0.1-5%, The balance is an alloy layer made of Zn and inevitable impurities, or in mass%, Al: 4 to 20%, Mg: 0 1~5%, Si: 0.0005~0.8%, and the balance plating layer having any of an alloy layer consisting of Zn and unavoidable impurities.

  For this purpose, the second stage hot dip galvanizing is desirably performed in the range of a bath temperature of 400 to 480 ° C. and an immersion time of 30 to 900 seconds.

  As a lower layer, an Fe—Al alloy layer, an Fe—Al—Zn alloy layer, an Fe—Al—Si alloy layer, an Fe—Al—Zn—Si alloy layer, and an alloy layer containing Mg in these alloy layers Any one of them, and as an intermediate layer, Al: 4 to 20%, Fe: 0.1 to 15%, Mg: 0.1 to 5%, the balance being Zn and inevitable Alloy layer consisting of mechanical impurities, or in mass%, Al: 4-20%, Fe: 0.1-15%, Mg: 0.1-5%, Si: 0.0005-0.8%, balance In order to form an alloy layer made of Zn and inevitable impurities, it is necessary to alloy the Fe—Zn alloy layer formed by the first plating in a two-stage plating bath.

  When the alloying of the Fe—Zn alloy layer is insufficient, the Fe—Zn alloy layer remains in the plating layer, and the Fe—Al alloy layer, the Fe—Al—Zn alloy layer, the Fe—Al—Si alloy. Any one of the layer, the Fe—Al—Zn—Si alloy layer, and the alloy layer containing Mg in these alloy layers is not sufficiently formed, resulting in insufficient plating adhesion.

  If the immersion time is too long, Fe in the plating layer diffuses into the bath and the intended plating layer cannot be obtained. Therefore, the immersion time is the Fe-Zn alloy layer formed by the first plating. It is desirable that the alloy is sufficiently alloyed.

  In addition, after performing the first stage of hot dip galvanizing, when performing the second stage of hot dip galvanized alloy plating, it is once cooled, the object to be plated is transferred to a dedicated hanger, and the second stage of hot dip galvanized alloy plating is performed. However, in consideration of productivity, after the first stage hot dip galvanization, the second stage hot dip galvanization is performed without cooling and maintaining the temperature of the object to be plated at 300 ° C. or higher. It is desirable to immerse in alloy plating.

Although there is no particular restriction on the adhesion amount of the hot dip zinc alloy plating, it is desirable that the adhesion amount of the plating is 100 to 2000 g / m ² in total from the viewpoint of corrosion resistance after plating. In particular, when high corrosion resistance is required, it is preferably 300 to 2000 g / m ² .

  As described above, the base steel of the present invention can be used for both hot-rolled steel and cold-rolled steel, and the steel types are Al-killed steel, Si-killed steel, ultra-low carbon steel added with Ti, Nb, and the like, and these Various steels such as high-strength steel and stainless steel to which a strengthening element such as P, Si, or Mn is added can be applied, but Si killed steel excellent in hot dip galvanizing and workability is particularly suitable.

  By mass%, C: 0.005 to 0.15%, Si: 0.15 to 0.25%, Mn: 0.40 to 1.6%, P: 0.04% or less, S: 0.04 % Or less, Al: 0.001 to 0.06%, N: 0.0080% or less, the steel material consisting of the balance Fe and unavoidable impurities is inexpensive and excellent in workability, and is suitable for a plating bath. Even if it is immersed for a long time, the appearance defect called “Yake” is unlikely to occur, so the base of hot-dip plated steel used mainly for piping, building materials, civil engineering, agriculture, and fishery is mainly used outdoors. Ideal as a steel material.

  The reason why the steel material having the above components is optimal as the base steel material is as follows.

  C: C is an effective element for ensuring strength. If the content is small, the effect is not exhibited, so 0.005% or more is desirable. More desirably, it is 0.01% or more. However, when C is added excessively, the strength becomes too high, the elongation is lowered, and the bending workability is deteriorated, so 0.15% or less is desirable.

  Si: Si is an important element in the present invention. From the viewpoint of hot dip galvanizing properties, 0.02% or less or 0.15 to 0.25% is preferable for preventing “burning” in which the Fe—Zn alloy layer develops.

  On the other hand, from the viewpoint of resistance to plating peeling during processing, when Si is added, the Fe—Zn alloy layer is uniformly developed in the first stage plating, and the difference between the maximum value and the minimum value is within 30 μm. As described above, in the present invention that effectively uses this Fe—Zn alloy layer, the adhesion between the plating layer and the ground iron is improved, so it is desirable to add Si to some extent.

  Therefore, Si is desirably 0.15 to 0.25%. A range of 0.18 to 0.23% is even better. Si is an element effective for obtaining a deoxidizer and strength.

  Mn: Mn is an element effective for obtaining strength. In order to make Si 0.15 to 0.25%, if the addition amount is small, the Mn / Si mass ratio becomes low and welding defects are likely to occur during welding, so 0.40% or more is desirable. On the other hand, if added excessively, the strength becomes too high, the elongation decreases, and the bending workability deteriorates.

  P: P is present in the steel as an impurity. However, if the amount exceeds 0.04%, central segregation increases, and cracks tend to progress from the inclusions during the forming process. % Or less is desirable. More desirably, it is 0.02% or less.

  S: S is also present in the steel as an impurity, but if its amount exceeds 0.04%, it causes cracking, so it is desirable to make it 0.04% or less. Furthermore, it is preferably 0.01% or less.

Al: Al is an effective and important element as a deoxidizer. If the added amount of Al is small, the effect cannot be obtained, so 0.001% or more is desirable. On the other hand, when Al is added excessively, an increase in Al ₂ O _{3 in} the steel is promoted and cleanliness is deteriorated.

  If N: N is contained excessively, AlN is generated and precipitated, causing cracking of the slab and generation of flaws, so 0.0080% or less is desirable. Furthermore, it is preferably 0.0060% or less.

  As described above, various shapes such as a wire shape such as a steel wire, a plate shape such as a steel plate, a net shape, a cylindrical shape such as a steel pipe, and a three-dimensional shape such as a rod shape can be used for the plated steel material. Use of steel pipes and the like that are used in severe corrosive environments after severe processing such as processing exhibits the effect of the product of the present invention having high corrosion resistance and excellent workability.

  Hereinafter, the present invention will be described specifically by way of examples.

Example 1
First, a steel pipe of SGP100A (thickness 4 mm, outer diameter 114.3 mm) is prepared, degreased and pickled with hydrochloric acid, and then immersed in an aqueous flux containing zinc chloride 50 g / l and ammonium chloride 150 g / l. Then, pretreatment was performed.

  Next, the pretreated steel pipe is immersed in a molten zinc bath at 450 ° C. for 3 to 10 minutes, and then Zn—Al—Mg with the Al amount, Mg amount, and Si amount changed at 400 to 450 ° C. It was immersed in a plating bath or a Zn—Al—Mg—Si plating bath for 30 to 600 seconds, pulled up, then cooled with water after a lapse of a certain time, and a hot dip galvanized steel pipe was produced.

  The component of the steel pipe was 0.08C-0.21Si-0.52Mn-0.012P-0.008S-0.002Al-0.003N.

  Table 1 and Table 2 (continuation of Table 1) show the plating composition and adhesion amount of the obtained hot-dip galvanized steel pipe. The adhesion amount of the plating was measured by a gravimetric method after dissolving the plating with hydrochloric acid containing an inhibitor. The composition of the plating layer was measured by chemical analysis after dissolving the plating with hydrochloric acid containing an inhibitor.

  The plating structure was observed using SEM and EPMA after polishing the C section of the steel pipe. The thickness of each layer of the plating layer was measured using a SEM in the range of 100 μm in the width direction, and the average value was used.

  As the composition of each layer of the plating layer, EPMA was used, a quantitative analysis was performed in a width direction of 100 μm with a beam diameter of 1 μm, and an average value thereof was used.

  It is difficult to determine the composition of the lower plating layer from EPMA because the thickness of the alloy layer is thin, but the layer in which the concentration of Al is detected is the Fe-Al alloy layer or Fe-Al -Zn alloy layer, a layer in which the enrichment of Al or Si is detected is a Fe-Al-Si alloy layer, a Fe-Al-Zn-Si alloy layer, or a layer in which the enrichment of Mg is detected. , Fe—Al—Mg alloy layer, Fe—Al—Zn—Mg alloy layer, Fe—Al—Si—Mg alloy layer, or Fe—Al—Zn—Si—Mg alloy layer.

  As for the plating adhesion of the processed part, flare processing was performed on the pipe end, and the plating adhesion of the inner and outer surfaces of the processed part was evaluated. The flare processing was performed by applying two-stage pipe expansion molding to the pipe end so that the steel pipe and the flange portion were 90 degrees. The width of the flange was 20 mm. The evaluation of the plating adhesion was carried out by performing a tape peeling test of the processed part and determining the transmittance of the tape after the test by the following rating. The score was 3 or more.

4: Transmittance of 90% or more 3: Transmittance of 70% or more and less than 90% 2: Transmittance of 50% or more and less than 70% 1: Transmittance of less than 50%

For corrosion resistance, the end face and the back face of a sample cut out in a length direction of 150 mm and a circumferential direction of 70 mm were sealed, and a salt spray test using 5% salt water was conducted for 200 hours to determine corrosion weight loss. Corrosion weight loss was calculated from the difference in weight before and after the test, and a corrosion weight loss of 20 g / m ² or less was accepted.

  The evaluation results are shown in Table 1 and Table 2 (continuation of Table 1). In Nos. 9, 22, and 35, the content of Al in the plating layer was outside the scope of the present invention, so the corrosion resistance was unacceptable. In Nos. 10, 23, and 36, since the Fe content of the alloy layer in the plating layer was outside the range of the present invention, the plating adhesion was unacceptable.

  In Nos. 11, 12, 24, 25, 37, and 38, the content of Mg in the plating layer was outside the scope of the present invention, so the corrosion resistance was unacceptable. Nos. 13, 26, and 39 indicate that the plating adhesion was unsuccessful because the lower layer in the plating layer was outside the scope of the present invention by shortening the immersion time of the second plating bath to 20 seconds. It was.

  The product of the present invention other than these was a hot dip galvanized steel material having both excellent corrosion resistance and high plating adhesion.

(Example 2)
First, a steel pipe of SGP100A (thickness 4 mm, outer diameter 114.3 mm) was prepared with the components shown in Table 3, and after degreasing and pickling with hydrochloric acid, zinc chloride 50 g / l, ammonium chloride 150 g / l Pretreatment was performed by dipping in an aqueous flux containing l.

  Next, the pre-treated steel pipe was immersed in a molten zinc bath at 450 ° C. for 3 to 10 minutes, and then Zn—Al— in which the Al amount, Mg amount, and Si amount were changed at 400 to 450 ° C. It was immersed in a Mg plating bath or a Zn—Al—Mg—Si plating bath for 30 to 600 seconds, pulled up, then cooled with water after a lapse of a certain time, and a hot dip galvanized steel pipe was produced.

  Table 3 shows the plating composition and adhesion amount of the obtained hot-dip galvanized steel pipe. The adhesion amount of the plating was measured by a gravimetric method after dissolving the plating with hydrochloric acid containing an inhibitor. The composition of the plating layer was measured by chemical analysis after dissolving the plating with hydrochloric acid containing an inhibitor.

  The plating structure was observed using SEM and EPMA after polishing the C section of the steel pipe. The thickness of each layer of the plating layer was measured using a SEM in the range of 100 μm in the width direction, and the average value was used. In addition, as for the variation of the intermediate layer, the difference between the maximum value and the minimum value of the thickness was measured.

  As the composition of each layer of the plating layer, EPMA was used, a quantitative analysis was performed in a width direction of 100 μm with a beam diameter of 1 μm, and an average value thereof was used. The lower plating layer was classified in the same manner as in Example 1 because the alloy layer was thin.

  The plating adhesion of the processed portion was evaluated by evaluating the plating adhesion of the inner surface and the outer surface of the processed portion by flaring the tube end. The flare processing was performed by applying two-stage pipe expansion to the end of the pipe so that the steel pipe and the flange were 90 degrees. The width of the flange was 20 mm. The evaluation of the plating adhesion was carried out by performing a tape peeling test of the processed part and determining the transmittance of the tape after the test by the following rating. The score was 3 or more.

4: Transmittance of 90% or more 3: Transmittance of 70% or more and less than 90% 2: Transmittance of 50% or more and less than 70% 1: Transmittance of less than 50%

For corrosion resistance, the end face and the back face of a sample cut out in a length direction of 150 mm and a circumferential direction of 70 mm were sealed, and a salt spray test using 5% salt water was conducted for 200 hours to determine corrosion weight loss. Corrosion weight loss was calculated from the difference in weight before and after the test, and a corrosion weight loss of 20 g / m ² or less was accepted.

  The evaluation results are shown in Table 3. In Nos. 13, 14, and 15, since the steel chemical components are outside the scope of the present invention, the plating adhesion was unacceptable. The product of the present invention other than these was a hot dip galvanized steel material having both excellent corrosion resistance and high plating adhesion.

Claims (14)

% By mass
C: 0.005 to 0.15%,
Si: 0.15-0.25%,
Mn: 0.40 to 1.6%
P: 0.04% or less,
S: 0.04% or less,
Al: 0.001 to 0.06%,
N: 0.0080% or less,
On the surface of the steel material composed of the remaining Fe and unavoidable impurities , an Fe—Al—Zn—Si alloy layer is provided as a lower layer, and an intermediate layer is further provided with an intermediate layer of mass%, Al: 4 to 20%, Fe: 0 0.1 to 15%, Mg: 0.1 to 5%, the balance having an alloy layer made of Zn and inevitable impurities, and further, as an upper layer, by mass%, Al: 4 to 20%, A plated steel material having high corrosion resistance and excellent workability, characterized by having an alloy layer composed of Mg: 0.1 to 5% and the balance being Zn and inevitable impurities. The plated steel material having high corrosion resistance and excellent workability according to claim 1, wherein the lower alloy layer contains Mg in the plated steel material having high corrosion resistance and excellent workability. 3. The plated steel material having high corrosion resistance and excellent workability according to claim 1, wherein Si is 0 in the intermediate layer or the alloy layer of any one of the intermediate layer and the upper layer. A plated steel material having high corrosion resistance and excellent workability, characterized by containing .0005 to 0.8%. The plated steel material having high corrosion resistance and excellent workability according to any one of claims 1 to 3 , wherein the thickness of the intermediate layer is twice or more the thickness of the upper layer. Plated steel with excellent corrosion resistance and workability. 5. The plated steel material having high corrosion resistance and excellent workability according to claim 4 , wherein the difference between the maximum value and the minimum value of the thickness of the intermediate layer is within 30 μm. Excellent plated steel material. A plated steel material having high corrosion resistance and excellent workability, wherein the plated steel material having high corrosion resistance and excellent workability according to any one of claims 1 to 5 is a steel pipe. It is a manufacturing method of the plating steel materials of any one of Claims 1-6, Comprising: In the two-step plating method which performs hot dip galvanization to the surface of steel materials, and performs hot dip galvanizing alloy plating, As a second stage, either a molten Zn-Al-Mg plating bath or a molten Zn-Al-Mg-Si plating bath is used as the second stage. A method for producing a plated steel material, characterized by immersing and performing hot dip zinc alloy plating.   8. The method for producing a plated steel material according to claim 7, wherein the hot dip galvanizing bath as the first stage is mass%, Zn: 99% or more, and the balance is an inevitable impurity. Manufacturing method. In the manufacturing method of the galvanized steel materials of Claim 7 , the hot dip galvanizing bath as a 1st step is a mass%, Al: 0.001-0.5%, and Ni: 0.001-0.2. %, 1 or 2, and the balance is Zn and unavoidable impurities. The method for producing a plated steel material according to any one of claims 7 to 9 , wherein the molten Zn-Al-Mg plating bath as the second stage is in mass%, Al: 4 to 20%, Mg: 0.00. A method for producing a plated steel material comprising 1 to 5%, the balance being Zn and inevitable impurities. The method of manufacturing a plated steel material according to any one of claims 7-9, molten Zn-Al-Mg-Si plating bath as a second stage, in mass%, Al: 4~20%, Mg : A method for producing a plated steel material comprising 0.1 to 5%, Si: 0.0005 to 0.8%, the balance being Zn and inevitable impurities. The method for producing a plated steel material according to any one of claims 7 to 11 , wherein the object to be plated is immersed in a hot dip galvanizing bath at a temperature of 430 to 500 ° C for 100 seconds or more in the first stage plating step. In the second stage plating step, the object to be plated is subjected to a molten Zn-Al-Mg plating bath having a temperature of 400 to 480 ° C or a molten Zn-Al-Mg-Si plating bath. A method for producing a plated steel material, characterized by performing hot dip zinc alloy plating by dipping for 30 seconds or more. 13. The method for producing a plated steel material according to claim 12 , wherein the object to be plated hot-plated in the first-stage plating step is hot-plated in the second-stage plating step while maintaining the temperature at 300 ° C. or higher. A method for producing a plated steel material. The method for producing a plated steel material according to any one of claims 7 to 13 , wherein the object to be plated is treated with a ferric chloride solution as a pretreatment.