JP2009120947A - Galvanized steel member having excellent corrosion resistance and weldability and coated steel member having excellent corrosion resistance - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a galvanized steel member having excellent corrosion resistance and weldability, and to provide a coated steel member having excellent corrosion resistance obtained by applying coating to the steel member. <P>SOLUTION: The galvanized steel member having excellent corrosion resistance and weldability is characterized in that the surface of a steel member is provided with a galvanized layer comprising, by mass, 1 to 10% Mg, 2 to 19% Al, 0.01 to 2% Si and 2 to 75% Fe, and the balance Zn with inevitable impurities. <P>COPYRIGHT: (C)2009,JPO&INPIT

Description

  The present invention relates to a surface-treated steel material excellent in corrosion resistance, a coated steel material coated on the steel material, in particular, a zinc-based alloy plated steel material excellent in corrosion resistance and weldability, and a coated steel material coated on the steel material.

  Zinc-based plated steel materials are used in a wide range of fields such as automobiles, home appliances, and building materials. However, in order to ensure a long-term rust prevention effect, zinc-based plating with a high adhesion amount is usually applied.

  The reason for this is that the corrosion rate of zinc-based plating is slower than that of steel, and zinc with a low corrosion potential exerts a sacrificial anti-corrosion function in places where the steel is exposed, so there is a large amount of zinc per unit area. This is because the corrosion resistance and anticorrosion effect obtained by the consumption of zinc can be maintained for a long time.

  Also, normally, when applying corrosion to steel to ensure corrosion resistance, in the coated steel, when flaws that reach the base iron occur in the coating, Corrosion with blistering may progress. Even in this corrosion form, the zinc-based plated steel material exhibits excellent corrosion resistance as compared with the bare steel material without plating, but for this corrosion resistance, it is advantageous that the plating has a high adhesion amount.

  However, when the zinc adhesion amount increases, the material properties such as workability and weldability of the steel material tend to deteriorate. Therefore, if possible, it is desirable to ensure high corrosion resistance with a lower adhesion amount plating. Therefore, many proposals have heretofore been made to add alloying elements to galvanizing to ensure sufficient corrosion resistance with a low adhesion amount.

  Actually, Zn—Ni alloy plating, Zn—Fe alloy plating, and the like are widely applied mainly to automobile steel plates, and Zn—Al alloy plating is widely applied mainly to building materials. Patent Documents 1 and 2 disclose plated steel materials in which Mg and Si are added to Zn—Al based alloy plating for further improvement of corrosion resistance.

  However, the addition of Al to the plating deteriorates the corrosion resistance against the progress of corrosion accompanied by swelling after coating. One reason for this is that, when Al is added at a high concentration, the chemical conversion treatment that is responsible for the adhesion between the plating layer and the coating film deteriorates, and the adhesion of the coating film is impaired.

  On the other hand, even if the amount of Al added is a relatively low concentration that can ensure sufficient chemical conversion treatment, the solubility of Al in an alkaline environment is higher than that of Zn. When the aqueous solution environment to which the plating is exposed is alkalized by this cathode reaction, the corrosion resistance of the plating deteriorates, and the problem that the progress of the swelling of the coating film is promoted occurs.

  Moreover, the addition of Al to the plating deteriorates the weldability of the plated steel material. In particular, the influence on the life of the electrode used in spot welding is great, and Non-Patent Document 1 discloses that the continuous spot property deteriorates as the Al content increases.

  Against this background, alloyed hot-dip galvanized steel sheets having improved spot weldability have been developed by alloying ground iron (Fe) and Zn in Zn-based plated steel sheets. In this steel sheet, the melting point of the plating layer is raised to a high temperature by alloying Fe and Zn, and the reaction with Cu of the welding tip (made of Cu alloy) is suppressed.

  However, in plating containing Al, Al is preferentially alloyed with Fe to form a barrier layer, and alloying of the entire plating layer is difficult to proceed. Therefore, until now, an iron-zinc alloy plated steel material subjected to zinc alloy plating containing 1% or more of Al has not been developed.

Japanese Patent No. 3179446 Japanese Patent No. 3561421 Toru Eriguchi, Soga So, Hiroshi Asada, Shoji Inoue: Nisshin Steel Engineering Reports, 72 (1995) p. 35-44

  The present invention suppresses deterioration of weldability and corrosion resistance against blistering after coating while maintaining the general effect of improving corrosion resistance due to the addition of Al in the plated layer of the zinc-based alloy-plated steel sheet. An object is to provide a zinc-based alloy-plated steel material excellent in weldability, and a coated steel material excellent in corrosion resistance obtained by coating the steel material.

  With reference to Patent Literature 1 and Patent Literature 2, the present inventors diligently developed a highly corrosion-resistant zinc-based alloy plated steel material excellent in spot weldability.

  One of the zinc-based alloy-plated steel materials is an alloyed hot-dip galvanized steel material with improved weldability of the plating layer. This is an alloy of zinc and ground iron (Fe) to form a high melting point Zn-Fe alloy plating layer, which significantly suppresses the Cu alloying reaction of the electrode tip (made of Cu alloy). is there.

  Even if the plating layer contains Al, it is considered that spot weldability is improved if zinc is alloyed with the base iron to form a high melting point plating layer, but the plating layer usually contains 1% of Al. When it contains above, a Fe-Al alloy layer will produce | generate at an interface with a ground iron, this will become a barrier layer, and alloying will not advance.

  Based on these facts, the present inventors have studied in detail the technique for enhancing the spot weldability, using heat treatment or alloying method by vapor deposition.

As a result, in zinc-based plating containing the required amount of Fe, by using a large-capacity induction heating device or the like, heat treatment to raise the temperature to high temperature at high speed or alloy plating by vapor deposition,
(I) the spot weldability of the plating layer is significantly improved, and
(Ii) improved corrosion resistance against blistering after painting;
I found.

  This invention was made | formed based on the said knowledge, The summary is as follows.

(1) On the surface of the steel material,
Mg: 1-10%
Al: 2 to 19%,
Si: 0.01-2%, and
A zinc-based alloy-plated steel material excellent in corrosion resistance and weldability, characterized by having a zinc-based alloy plating layer containing Fe: 2 to 75%, the balance being Zn and inevitable impurities.

(2) The zinc-based alloy plating layer contains, in mass%, Fe: 2 to 72%, and Fe, Mg, and Al in the plating layer are represented by the following formulas:
Fe (%) + Mg (%) + Al (%) ≦ 75
The zinc-based alloy plated steel material having excellent corrosion resistance and weldability as described in (1) above.

  (3) The zinc-based alloy plating layer having excellent corrosion resistance and weldability according to (1) or (2), wherein the zinc-based alloy plating layer contains Fe: 2 to 50% by mass%. Steel material.

  (4) The zinc-based alloy plating layer is excellent in corrosion resistance and weldability according to any one of (1) to (3), wherein the zinc-based alloy plating layer contains Fe in an amount of 20% by mass. Zinc-based alloy plated steel.

(5) The zinc-based alloy having excellent corrosion resistance and weldability according to any one of (1) to (4), wherein Mg ₂ Si is dispersed in the zinc-based alloy plating layer Plated steel.

(6) The zinc-based alloy plating layer is further in mass%,
Ca: 0.01 to 0.5%,
Ti: 0.01-0.2%
Cu: 0.1 to 1.0%
Ni: 0.01-0.2%
Co: 0.01 to 0.3%
Cr: 0.01 to 0.2%, and
Mn: zinc-based alloy-plated steel material excellent in corrosion resistance and weldability according to any one of (1) to (5), characterized by containing one or more of 0.01 to 0.5% .

  (7) A chemical conversion coating layer is formed as an intermediate layer on the zinc-based alloy plated steel layer of the zinc-based alloy-plated steel material according to any one of (1) to (6), and an organic layer is further formed thereon. Painted steel material with excellent corrosion resistance, characterized by forming a coating layer.

  According to the present invention, a zinc-based alloy-plated steel material excellent in corrosion resistance and weldability, and a coated steel material excellent in general corrosion resistance after coating and excellent in corrosion resistance against swelling from the buttock, which is applied to the steel material Can be provided.

  Hereinafter, the present invention will be described in detail.

  The zinc-based alloy-plated steel material of the present invention (the present invention-plated steel material) is, on the surface of the steel material, in mass%, Mg: 1 to 10%, Al: 2 to 19%, Si: 0.01 to 2%, and Fe: 2 to 75% is contained, and the balance has a zinc-based alloy plating layer made of Zn and inevitable impurities.

  First, the reason for limitation related to the component composition of the zinc-based alloy plating layer will be described. Hereinafter, “%” means mass%.

  Mg is added to increase the corrosion resistance of the plating layer. If Mg is less than 1%, the effect of improving corrosion resistance is not manifested, so the lower limit is made 1%. On the other hand, if Mg exceeds 10%, it is too much, the plating layer becomes brittle, and the adhesion decreases, so the upper limit is made 10%. Preferably, it is 3 to 6%.

In order to disperse Mg ₂ Si contributing to the improvement of corrosion resistance in the solidified structure of the plating layer, the Mg content is preferably 3% or more.

  Al is added to increase the corrosion resistance of the plating layer and to impart the required strength and toughness to the plating layer. If Al is less than 2%, the required strength and toughness cannot be obtained, the plating layer becomes brittle, and the adhesion decreases, so the lower limit is made 2%. On the other hand, if Al exceeds 19%, the effect of improving corrosion resistance is saturated, so the upper limit is made 19%. Preferably, it is 5 to 15%.

In order to disperse Mg ₂ Si contributing to the improvement of corrosion resistance in the solidified structure of the plating layer, Al is preferably 4% or more.

  Si is added to suppress the reaction between Al in the plating and Fe in the steel sheet and to secure the adhesion between the steel sheet and the plating layer. When Si is less than 0.01%, Al in the plating reacts with Fe in the steel sheet to make the plating layer brittle and lower the adhesion, so the lower limit is made 0.01%. On the other hand, if Si exceeds 2%, the adhesion improving effect is saturated, so the upper limit is made 2%.

  Fe is added to increase the spot weldability of the plating layer and to increase the corrosion resistance against swelling after coating. If the Fe content is less than 2%, the above improvement effect does not appear remarkably, so the lower limit is made 2%. From the viewpoint of spot weldability and blistering corrosion resistance after coating, Fe is more preferably more than 20%.

  On the other hand, if Fe exceeds 75%, the corrosion potential of the plating layer becomes close to the corrosion potential of the base iron, and the sacrificial anticorrosive ability decreases, so the upper limit is made 75%. The content of Fe is preferably 2 to 72% and more preferably 2 to 50% in relation to the contents of Mg and Al described below.

Further, from the viewpoint of manufacturability, the Fe content is preferably within 3 times the Al content. This is because an intermetallic compound (Al ₅ Fe ₂ phase or AlFe phase) in this component range is relatively easily formed even by a short alloying heat treatment. If the Fe content exceeds 3 times the Al content, the heat treatment time for alloying is too long, which may be impractical.

  The suitable content of Fe in the plating layer based on these is mass%, more than 20% and not more than 50%.

In the present plated steel material, the contents of Fe, Mg, and Al in the plating layer are as follows:
Fe (%) + Mg (%) + Al (%) ≦ 75%
It is preferable to satisfy.

  If the total amount of Fe, Mg, and Al exceeds 75%, the amount of Zn in the plating layer becomes relatively small, and the sacrificial anticorrosive effect of Zn is reduced, and the corrosion resistance is lowered. Therefore, the upper limit of the total amount is set to 75%.

In the plated steel material of the present invention, when the contents of Al, Mg, and Si are increased and Mg ₂ Si is dispersed in the solidified structure of the plating layer, the corrosion resistance is further improved. Mg ₂ Si is an intermetallic compound that can be observed with a clear island-like outline in the solidification structure of the plating layer with an optical microscope, and is the first shown in the Al—Mg—Si ternary equilibrium diagram. It is crystalline Mg ₂ Si.

The primary crystal Mg ₂ Si greatly contributes to the improvement of the corrosion resistance of the plating layer. This is because Mg ₂ Si is a very active intermetallic compound.

A Zn—Al—Mg—Fe alloy other than Mg ₂ Si, which forms the matrix phase of the plated metal, has a Zn phase, Al phase, Zn—Fe phase (Γ phase, δ, depending on the degree of alloying with Fe. Phase, ζ phase, etc.), Al—Fe phase (mainly Al ₅ Fe ₂ phase, Al ₃ Fe ₄ phase, AlFe phase), Mg—Zn phase (mainly MgZn ₂ phase). However, all of these have a higher potential than the Mg ₂ Si phase, and the Mg ₂ Si phase reacts preferentially with water.

That is, in a corrosive environment, active Mg ₂ Si reacts with water and decomposes, and the matrix metal structure of the plating, which is a Zn—Al—Mg—Fe alloy, is prevented by sacrificial anticorrosive action. It is considered that Mg hydroxide generated by the reaction forms a protective film and suppresses the progress of corrosion.

In order to disperse a required amount of active Mg ₂ Si in the solidified structure of the plating layer, as described above, Mg is preferably 3% or more, and Al is preferably 4% or more.

  In the plated steel material of the present invention, one or more of Ca, Ti, Cu, Ni, Co, Cr, and Mn are added to the plating layer in order to improve the corrosion resistance after coating.

  When these elements are present in the plating layer, (a) the thin film formed on the surface of the plating layer is more passivated, the corrosion of the plating layer under the thin film is delayed, and (b) the thin film is formed with the plating layer. Suppresses the reaction at the interface of the coating to stabilize the coating and / or (c) the surface of the plating layer has fine irregularities, and the fine irregularities exert an anchoring effect on the coating Thus, the corrosion resistance after painting is improved.

  The effect of improving the corrosion resistance after painting is manifested by adding 0.01% or more for Ca, Ti, Ni, Co, Cr, and Mn, and manifesting by 0.1% or more for Cu. .

  On the other hand, when the addition amount increases, the appearance after plating becomes rough. For example, poor appearance occurs due to adhesion of dross, oxide, etc., so the upper limit of the addition amount is Ca: 0.5%, Ti: 0.2%, Cu: 1.0%, Ni: 0.2%, Co: 0.3%, Cr: 0.2%, Mn: 0.5%.

  In addition, about Pb, Sn, and Sb in a plating layer, it is desirable to suppress to 0.1% or less, 0.02% or less, and 0.1% or less, respectively.

  This is because when the amounts of Pb, Sn, and Sb are suppressed in the plating bath, the initial plating and the initial reactivity of the steel material surface are improved, and alloying easily proceeds.

  The hot dip plating method according to the present invention is not limited to a specific plating method as long as a plating layer having a desired composition and characteristics can be formed. Regardless of the plating method such as the Sendzimir type, the flux type, or the pre-plating type, a hot dipping method can be used.

  A normal non-oxidizing furnace type hot-dip plating method is preferable, but a pre-plating method in which Ni pre-plating is applied as a lower layer can also be used. When the pre-plating method is used, it is preferable that after the pre-Ni plating is applied to the base steel material, rapid and low-temperature heating is performed in a non-oxidizing or reducing atmosphere, and then hot-dip plating is performed.

In order to disperse primary Mg ₂ Si in the solidified structure of the plating layer, Mg and Al in the plating bath are 3% or more and 4% or more, respectively, and the bath temperature is 450 ° C. or more and 650 ° C. or less. The cooling rate after plating is preferably 0.5 ° C./second or more.

By setting Mg and Al in the plating bath to 3% or more and 4% or more, respectively, primary crystal Mg ₂ Si can be surely dispersed in the solidified structure of the plating layer.

When the bath temperature is lower than 450 ° C., primary Mg ₂ Si cannot be crystallized, and when it exceeds 650 ° C., a coating is formed on the plating surface and the appearance is deteriorated. A larger cooling rate is preferable because the crystal becomes finer. However, in order to crystallize the primary Mg ₂ Si, it is necessary to maintain a cooling rate of 0.5 ° C./second or more.

The coating amount of the plated steel material of the present invention is preferably 10 g / m ² or more from the viewpoint of ensuring corrosion resistance, and is preferably 150 g / m ² or less per side from the viewpoint of ensuring spot weldability. The smaller the amount of adhesion, the better the spot weldability, but an amount of adhesion of 10 g / m ² or more per side is required from the viewpoint of ensuring corrosion resistance. In order to maintain a good balance between corrosion resistance and spot weldability, the amount of plating is preferably 15 g / m ² or more and 70 g / m ² or less.

  When the plated steel material of the present invention is used in a normal usage method, plating is performed on the entire surface of the steel material, for example, on both surfaces in the case of a steel plate, but the corrosion resistance of one surface of the steel plate is reliably guaranteed by coating or the like. When it exists, you may plate only on the single side | surface of a steel plate. That is, an aspect in which a part of the surface of the steel material is plated is also within the scope of the plated steel material of the present invention.

  The steel material used as the base material of the plated steel material of the present invention is not limited to a specific steel material. For example, Al killed steel materials, ultra-low carbon steel materials, high carbon steel materials, various high-tensile steel materials, Ni / Cr-containing steel materials and the like can be used regardless of mechanical characteristics and material characteristics. Moreover, there is no restriction | limiting in particular also about pre-processing methods, such as the steel manufacturing method, hot rolling method, pickling method, and cold rolling method which concern on manufacture of the said steel materials.

  Here, the coated steel material of the present invention (the coated steel material of the present invention) forms a chemical conversion coating layer as an intermediate layer on the zinc-based alloy plating layer of the plated steel material of the present invention, and further, an organic coating layer thereon Is formed.

  The chemical conversion coating layer as an intermediate layer of the coated steel sheet can be formed by using a zinc phosphate chemical conversion treatment, a coating chromate treatment, an electrolytic chromic acid treatment, a reaction chromate treatment, a chromate-free chemical conversion treatment, or the like.

  As a chromate-free chemical conversion coating layer, a layer treated with an aqueous solution containing a silane coupling agent, a zirconium compound, a titanium compound, tannin or tannic acid, a resin, silica and the like is known. JP, JP 9-241576, JP 2001-89868, JP 2001-316845, JP 2002-60959, JP 2002-38280, JP 2002-266081. Alternatively, a known processing technique described in JP 2003-253464 A may be used.

These chemical conversion treatments are commercially available, for example, chromate treatment “ZM-1300AN” manufactured by Nippon Parkerizing Co., Ltd., chromate-free chemical conversion treatment “CT-E300N” manufactured by Nippon Parkerizing Co., Ltd., and trivalent chromium-based chemical conversion manufactured by Nippon Paint Co., Ltd. The treatment can be performed using “Surfcoat ^™ NRC1000” or the like.

  The upper organic coating layer of the coated steel sheet can be formed using a polyester resin, an amino resin, an epoxy resin, an acrylic resin, a urethane resin, a fluorine resin, or the like, and is not particularly limited to a specific resin film. However, a thermosetting resin coating is most preferable as the organic coating on the coated steel sheet to be subjected to strong processing.

  The thermosetting resin coating film can be formed using polyester-based paints such as epoxy polyester paints, polyester paints, melamine polyester paints, urethane polyester paints, and acrylic paints.

  Polyester-based paints in which part of the acid component of the polyester resin is replaced with fatty acids, oil-free alkyd resins that are not modified with oil, melamine resin or polyisocyanate resin as a curing agent, and various crosslinking agents Since the combined acrylic paint has better processability than other paints, the organic coating layer formed with these paints does not crack or the like even when subjected to severe processing.

  The film thickness of the organic coating layer is preferably 1 to 100 μm. If the film thickness is less than 1 μm, it is difficult to ensure corrosion resistance, while if the film thickness exceeds 100 μm, it is disadvantageous in terms of cost. The organic coating layer may be a single layer or multiple layers, and the film thickness is preferably 20 μm or less.

  In addition, you may mix | blend additives, such as a plasticizer, antioxidant, a heat stabilizer, an inorganic particle, a pigment, and organic lubrication, with an organic coating layer as needed.

  Next, examples of the present invention will be described. The conditions of the examples are one example of conditions adopted for confirming the feasibility and effects of the present invention, and the present invention is limited to this one example of conditions. Is not to be done. The present invention can adopt various conditions as long as the object of the present invention is achieved without departing from the gist of the present invention.

Example 1
Surface treatment having a cold-rolled steel sheet having a thickness of 0.8 mm, an equilateral mountain-shaped steel having a thickness of 10 mm and a side length of 10 cm, and a hot-rolled steel sheet having a thickness of 10 mm as a base material and having an alloy plating layer shown in Table 1 Steel was produced.

When a cold-rolled steel sheet having a thickness of 0.8 mm is used as a base material, a Zn-Mg-Al-Si plating bath in which the amount of Mg, Al, and Si in the bath is changed at a bath temperature of 400 to 600 ° C. After being dipped for 3 seconds and pulled up, nitrogen gas was sprayed to adjust the adhesion amount after alloying to 50 g / m ² .

For example, when an alloy plating layer of Fe: 10% is formed, 45 g / m ² of plating components other than Fe are adhered, and then rapidly heated in an induction heating furnace and subjected to alloying heat treatment. 5 g / m ² min of Fe was contained in the plating layer, and the adhesion amount of the plating layer after alloying was 50 g / m ² . The Fe concentration was adjusted by controlling the degree of alloying by adjusting the temperature and holding time of the alloying heat treatment in the induction heating furnace.

  In addition, the holding time of the alloying heat treatment required for obtaining a predetermined Fe concentration was used as an evaluation index for manufacturability, and when this holding time exceeded 20 seconds, there was a manufacturability problem (Δ), 20 seconds. Those obtained with a predetermined composition by the heat treatment within the range are shown in Table 1 together with other performance evaluation results as good manufacturability (◯).

  The adhesion amount and the component composition of the plated layer of the obtained plated steel sheet were confirmed by the mass change before and after acid peeling of the plating layer and the analysis result obtained by analyzing the solution by ICP after acid peeling. The component composition of the plating layer of the obtained plated steel sheet is also shown in Table 1.

  The equilateral angle steel was cut at 10 cm in the longitudinal direction, and the hot rolled steel sheet was cut into a 10 cm × 10 cm square to prepare a sample. Using a crucible furnace, the sample was subjected to soaking plating by the flux method. The plating adhesion amount was adjusted by adjusting the dipping time and the drawing speed. The alloying heat treatment was separately performed using an induction heating furnace.

  The prepared sample was subjected to the following evaluation test.

The dispersion of Mg ₂ Si in the plating layer was confirmed by SEM observation of the test piece in which the sample was embedded.

Since Mg ₂ Si is dispersed in islands, it can be easily determined from the shape, but the components were further analyzed by EDX.

In the range of EDX detection components, when it is confirmed that 80% or more is Mg and Si and the atomic component ratio of Mg and Si is 1.5: 1 to 3: 1, the dispersion of Mg ₂ Si Yes (O).

The above-mentioned range was given to the atomic component ratio because of the influence of other phases (intermetallic compounds, precipitates, etc.) due to the influence of grain size and depth direction during analysis. This is because it can be specified that the observation object is Mg ₂ Si.

  The corrosion test of the bare steel plate is conducted in accordance with the salt spray test (SST) described in JIS-Z-2371, and the corrosion weight loss after 300 hours of the salt water concentration test is 10 g / L. Evaluated.

Corrosion weight loss of less than 2 g / m ² is “◎”, 2-5 g / m ² is “◎”, 5-10 g / m ² is “◯”, and 10 g / m ² or more is “x”. .

  In the coating film swelling test, the test material was degreased with a commercially available alkaline degreasing solution (pH = 10.5, 40 ° C., 1 minute immersion), and then subjected to a chemical conversion treatment for automobiles (Surfdyne 2500MZL manufactured by Nippon Paint). After applying the cationic electrodeposition coating for automobile (Nihon Paint V20, 20μm, baking at 170 ° C for 20 minutes) and letting it stand all day and night, it penetrates the coating and plating with a cutter knife on one side of the test material. An 80 mm long straight wrinkle was formed and subjected to a combined cycle corrosion test in accordance with SAE J2234.

  Corrosion resistance after coating was evaluated by the swollen width of the coating film after 3000 hours. The maximum blister width of less than 3 mm was “◎”, 3 mm or more and less than 5 mm was “◯”, and 5 mm or more was “x”.

  The spot welding test was conducted by investigating the number of consecutive dots during spot welding under the following welding conditions. A Cu—Cr electrode having a tip diameter of 4.5 mmφ, a tip angle of 120 degrees, and an outer diameter of 13 mmφ was used. Ten cycles of energization were performed using a 50 Hz power source. Pressurization was performed at a pressure of 1.7 kN for 30 cycles before energization, 10 cycles after energization, and without an up-down slope.

In addition, the welding current value in the continuous spot property investigation is the current value I ₁ (kA) that gives the nugget diameter indicated by 4√t when the plate thickness is t (mm), and the welding current value I ₂ (kA). ) Was used to determine the maximum number of hit points at which a nugget diameter of 4√t was maintained.

Those with a continuous score of 8000 points or more, especially “Excellent spot weldability”, “◎◎”, less than 8000 points, but with a score of 6000 points or more, “A” indicates that the number of consecutive hit points of 3000 points or more was obtained, but “B” was not satisfied. Those that did not reach 3000 points were marked with “x”.
The evaluation results of each test are also shown in Table 1.

  As shown in Table 1, the steel material of the present invention has excellent bare corrosion resistance, post-coating corrosion resistance, and weldability. Further, among the steel materials of the present invention, steel materials having a plating layer with Fe / Al of 3 or less had good manufacturability. The comparative steel material has poor corrosion resistance even if it has good corrosion resistance, poor weldability, or excellent weldability.

(Example 2)
No. in Table 1 Using the plating bath having the component composition shown in 3, 5, 19, and 21, the effect of the additive element was investigated.

  High purity metal powder or an alloy with Al was added to the plating bath, and the elements shown in the other columns of Table 2 were added. Other conditions are the same as in the first embodiment.

  The produced plated steel sheet was subjected to the same film swelling test as in Example 1. However, the chemical conversion treatment and painting were changed as follows.

(A) Chemical conversion treatment A chromate-free chemical conversion treatment solution “CT-E300N” manufactured by Nihon Parkerizing Co., Ltd. was applied with a roll coater and dried in a hot air oven. The drying conditions in the hot air oven were 60 ° C., the ultimate plate temperature of the steel plate. The chromate-free coating was applied so that the amount of adhesion was 200 mg / m ^{2 in} terms of the total solid content.

(B) Primer A clear paint of FL641EU primer manufactured by Nippon Fine Coatings Co., Ltd. was prepared, and “K-WHITE # 105” (hereinafter referred to as “phosphorus aluminum trihydrogen phosphate manufactured by Teika Co., Ltd.) as a chromate-free anticorrosive pigment. Acid AL ”) and“ SHIELDEX C303 (registered trademark) ”(hereinafter referred to as“ Ca silica ”), which is a calcium ion exchange silica manufactured by GRACE, were applied with a roll coater so that the dry film thickness was 5 μm. Then, it was baked in a hot air oven under conditions where the ultimate plate temperature was 215 ° C.

  In addition, Al phosphate was added so that it might become 25 mass% in the dry coating film of a primer, and Ca silica was added so that it might become 25 mass% in the dry coating film of a primer.

(C) Top White paint of “Flexcoat 100HQ (registered trademark)”, a paint for precoated steel sheets manufactured by Nippon Fine Coatings Co., Ltd., is applied with a roll coater to a dry film thickness of 15 μm. Then, baking was performed under the condition that the ultimate plate temperature was 230 ° C.

  On one side of the coated test piece, a straight wrinkle with a length of 80 mm that penetrated the coating and plating with a cutter knife to reach the base steel was formed, and a combined cycle corrosion test in accordance with SAE J2234 was performed.

  Corrosion resistance after coating was evaluated by the swollen width of the coating film after 3000 hours. Those with a maximum swollen width of less than 1 mm are designated as “◎◎”, those with a maximum swollen width of from 1 mm to less than 3 mm are designated as “◎”, those having a maximum swollen width of from 3 mm to less than 5 mm are designated as “◯”, " The evaluation results are shown in Table 2.

  As shown in Table 2, the ones with added elements (No. with subscripts a, b, c) have improved post-coating corrosion resistance compared to those without added elements. .

  As described above, according to the present invention, the zinc-based alloy-plated steel material excellent in corrosion resistance and weldability, and the steel material coated, the general corrosion resistance after coating is excellent, and the corrosion resistance against swelling from the buttock In addition, it is possible to provide an excellent coated steel material.

  Therefore, the steel material of the present invention can be widely applied to automobiles, buildings, houses, etc., while maintaining the same productivity as the conventional one, extending the life of the members, effectively using resources, and reducing the environmental load. It contributes to the development of industry because it contributes to reduction of maintenance labor and cost.

Claims (7)

On the surface of the steel material,
Mg: 1-10%
Al: 2 to 19%,
Si: 0.01-2%, and
A zinc-based alloy-plated steel material excellent in corrosion resistance and weldability, characterized by having a zinc-based alloy plating layer containing Fe: 2 to 75%, the balance being Zn and inevitable impurities. The zinc-based alloy plating layer contains, by mass%, Fe: 2 to 72%, and Fe, Mg, and Al in the plating layer are represented by the following formula:
Fe (%) + Mg (%) + Al (%) ≦ 75
The zinc-based alloy-plated steel material having excellent corrosion resistance and weldability according to claim 1.   The zinc-based alloy plated steel material having excellent corrosion resistance and weldability according to claim 1 or 2, wherein the zinc-based alloy plating layer contains Fe: 2 to 50% by mass.   The zinc-based alloy plating layer according to any one of claims 1 to 3, wherein the zinc-based alloy plating layer contains 20% by mass and Fe in excess of 20%. Steel material. 5. The zinc-based alloy-plated steel material having excellent corrosion resistance and weldability according to claim 1, wherein Mg ₂ Si is present in a dispersed manner in the zinc-based alloy plating layer. The zinc-based alloy plating layer is further in mass%,
Ca: 0.01 to 0.5%,
Ti: 0.01-0.2%
Cu: 0.1 to 1.0%
Ni: 0.01-0.2%
Co: 0.01 to 0.3%
Cr: 0.01 to 0.2%, and
The zinc-based alloy-plated steel material having excellent corrosion resistance and weldability according to any one of claims 1 to 5, comprising Mn: 0.01-0.5% or two or more.   A chemical conversion treatment coating layer is formed as an intermediate layer on the zinc-based alloy plating layer of the zinc-based alloy plating steel material according to any one of claims 1 to 6, and an organic coating layer is further formed thereon. Painted steel with excellent corrosion resistance characterized by