KR100411477B1 - Metal cored wire for welding of austenitic stainless steel - Google Patents

Abstract

The disclosed invention relates to a metal cored wire for austenitic stainless steel welding, wherein the outer shell of the wire is made of low carbon stainless steel, and the flux filled in the outer shell is C: 0.02% or less, P: 0.02, based on the total weight of the wire. % Or less, S: 0.01% or less, Cr: 5.0 to 12%, Ni: 1.0 to 6.0%, Mn: 0.3 to 1.5%, at least one of MgO, Na ₂ O, K ₂ O, and CaO which are alkali oxides 0.1 to 1.0%, iron and arc stabilizers: 0.1 to 10%, oxides of TiO ₂ + SiO ₂ + Al ₂ O ₃ : 0.1 to 3.0%, but TiO ₂ , SiO ₂ , Al ₂ O ₃ and Mn are added Provided is an austenitic stainless steel welded metal cored wire characterized in that the combination ratio (A) of the following formula (1) satisfies 0.3 to 3.0.

Equation (1)

According to the present invention, in addition to the advantages of deoxidation effect, welding workability, welding material cost, manufacturing efficiency and the like of the stainless steel flux cored wire, a metal cored wire for stainless steel welding is improved.

Description

Metal cored wire for austenitic stainless steel welding {Metal cored wire for welding of austenitic stainless steel}

The present invention relates to a metal cored wire for welding austenitic stainless steel, metal cored used in the nuclear industry, thermal power industry, chemical plants as well as for welding of critical parts, such as seawater structures, or for welding thin plates of mild steel and stainless steel It is about a wire. In particular, the invention relates to an austenitic stainless steel welded metal cored wire designed for its use, with an emphasis on welding workability, spatter generation amount and arc stability, to be suitable for welding of a portion sensitive to spatter generation amount.

Conventionally, many welding materials for stainless steel have appeared due to the demand for improvement of various device efficiency, stability, and durability, and in particular, the stainless steel can be quickly made to meet the requirements of excellent work efficiency and good welding workability in terms of welding construction. Steel welding materials have been provided.

In the case of austenitic stainless steel flux cored wire, it shows good welding workability when multi-layer welding and there is no contact with atmospheric atmosphere by the gas shield, strong fault resistance by slag coating, high temperature toughness and corrosion resistance, and strong acidic atmosphere. There is an advantage in enduring the situation is expanding its use. In addition, metal inert gas arc welding (MIG) materials have been continuously improved in terms of welding method, improving welding efficiency, expanding welding execution area, improving welding workability, and welding bead shape.

On the other hand, in the prior art, it is suggested that the production efficiency is increased by improving the hot workability when manufacturing MIG wires (Japanese Patent Laid-Open No. 4-143255), and the welding workability is excellent under high current welding conditions, and the amount of spatter generated is increased. It is proposed that the reduction was remarkable (Japanese Patent Laid-Open No. 5-96397). In the case of MIG welding materials, anti-wormhole resistance has been improved by adjusting the chemical composition of the wire rod, and non-magnetic steel welding materials having excellent high temperature crack resistance, high temperature strength, and high temperature toughness have emerged.

However, in recent stainless steel market trends, as well as 50kg thick plates and 70-80kg stainless steels, welding materials are being developed accordingly in terms of mechanical properties and other characteristics. Many reach it. In addition, due to the corrosion resistance of austenitic stainless steel, the use of 1-6 tons of thin plate is increasing among 12 tons of stainless steel with the diversification of its use, and the corresponding welding material is MIG / including flux cored wire. A large number of TIG welding materials have appeared and are currently used. In the case of thin plates, arc stability, spatter generation amount, and beautiful bead shape are required during welding, and accordingly, it is required to pull in the welding material for stainless steel, low temperature impact resistance and welding workability, and especially 1-pass. It requires high convenience and advanced slag peelability in welding. Therefore, in many welding methods such as MIG / TIG, GMAW, SMAW, SAW, etc., it can be applied to many parts such as arc stability, slag peeling resistance, blowhole resistance, spatter generation reduction, fume generation reduction, high temperature / low temperature toughness, etc. Design is focused on, and many products that solve the above problems are appearing for the purpose.

In the case of many conventional stainless steel welding, the thickness of 1 ~ 6t sheet is particularly sensitive to the spatter generation such as automobile parts, and if spatter occurs, the spatter must be removed by grinding by hand. In welding, the welding method is MIG / TIG or GMAW. In the case of the TIG welding method, spatter generation can be significantly reduced, but the work efficiency is very low, and only a small amount is applied to the important part. In case of MIG welding method, Ar gas or inert gas containing 1 ~ 5% O ₂ in Ar gas is used to bring the arc transition form to the spray type. It is widely used. However, the MIG welding material has a narrow welding operating condition, and in the vicinity of the spray transition section in the low current region, arcs short-circuit and spray transition coexist so that spatter is generated and the sound is severe during welding. In addition, the spray shape can be maintained in the high current region, but the arc is unstable and the welding is not good or the penetration is shallow. That is, it is difficult to satisfy a welding material having good welding workability in both low current and high current regions, and it is impossible to apply it in various welding conditions. In addition, there are limitations in diversifying the product depending on the chemical composition of raw materials or the surface condition of raw materials. In the manufacturing process, high speed drawing is impossible due to work hardening problem of stainless steel raw materials. The manufacturing process is also less efficient. In addition, the cost of raw materials is high, and the cost of welding materials is high due to the decrease in productivity. Nowadays, the welding contractor, which used many MIG wires, is shifting to the form of flux cored stainless steel welding material.

In the case of stainless flux cored wire, the arc stabilizer or slag generating agent is used to improve various welding workability and welding efficiency. However, since 100% CO ₂ is used as the shielding gas, it is a problem in environmentally friendly parts. It is becoming. In addition, there is an additional process that burdens workers in removing the amount of slag generated after welding.

The present invention has been proposed in view of the above problems, and in addition to the advantages of deoxidation effect, welding workability, welding material cost, and manufacturing efficiency of stainless flux cored wire, the metal for welding stainless steel is improved in welding efficiency. It is an object to provide a cored wire.

The above object of the present invention is an austenitic stainless steel welded metal cored wire, the outer shell of the wire is made of low carbon stainless steel, the flux filled in the inner shell is C: 0.02% or less relative to the total weight of the wire, P: 0.02% or less, S: 0.01% or less, Cr: 5.0-12%, Ni: 1.0-6.0%, Mn: 0.3-1.5%, at least one of alkali oxides MgO, Na ₂ O, K ₂ O, CaO 0.1 to 1.0%, iron and arc stabilizer: 0.1 to 10%, the sum of oxides of TiO ₂ + SiO ₂ + Al ₂ O ₃ : 0.1 to 3.0%, but TiO ₂ , SiO ₂ , Al ₂ O ₃ and Mn is achieved by the austenitic stainless steel welded metal cored wire, characterized in that the combination ratio (A) of the following formula (1) satisfies 0.3 to 3.0.

Equation (1)

The present invention is a metal cored wire sheath filled with a flux in a stainless steel sheath, C≤0.02%, Si≤1.0%, Mn≤2.0%, P≤0.045%, S≤0.03%, Ni: 9.0-13.0%, Low carbon stainless steel according to JIS G4305 standard containing Cr: 18.0 to 20.0% is used.

Hereinafter, the role of each component and the reason of numerical limitation according to the above structure of this invention are demonstrated. % Means weight% unless otherwise specified.

The sheath used in the present invention is similar to that used for the conventional stainless flux cored wire sheath, which is C≤0.02%, Si≤1.0%, Mn≤2.0%, P≤0.045%, S≤ according to JIS G4305 standard. 0.03%, Ni: 9.0-13.0%, Cr: 18.0-20.0%. By using this sheath and heat-treating at 1000 ℃ or higher, work hardening problem can be solved.

In addition, the reason for using the low carbon stainless steel in the present invention is as follows.

The reason for specifying C to be 0.02% or less is to make the transition form of the arc into a dispersion type (spray form) even under low current and low voltage conditions. In addition, when the content of C is high, C in the skin is defined to be less than 0.02% because it combines with Ti, Mo, N, Cr to form carbides or carbonitrides to decrease toughness and cause cracking. Si serves to improve the workability by controlling the Si content contained in the weld metal and generating a small amount of SiO ₂ at the time of welding, but in order to beautify the appearance of the bead, it is preferable to specify 1.0% or less. Mn not only serves as a deoxidizer, but also contributes to the improvement of arc stability together with TiO ₂ and SiO ₂ and may form a small amount of MnO to affect the appearance of beads. In the case of P and S, there is a problem of lowering toughness and cracking as impurities, so that the respective contents are defined as P ≦ 0.045% and S ≦ 0.03%. In particular, the above-mentioned content is preferable in consideration of manufacturing cost. In the case of Ni and Cr, the above specification is defined in consideration of the suitability of the chemical composition contained in the weld metal and the welding material for welding the dissimilar materials.

Next, the flux composition of this invention is demonstrated.

C: 0.02% or less, P: 0.02% or less, S: 0.01% or less

It is known to add Nb as a method of reducing brittle cracks, high temperature cracks, and the like commonly generated in welds (Japanese Patent Laid-Open No. 7-124785). However, the inventors of the present invention consider the solid solution limits of C and N in the face centered cubic structure of austenite, and thus, when limiting the contents of C and N and controlling extremely small amounts of impurities such as P and S, Nb is added. It has been found that it is possible to significantly reduce the occurrence of weld cracking if not. C in the flux combines with Ti, N, Cr, Mo and the like to form carbides or carbonitrides to reduce toughness and cause cracking, so the C content in the flux is preferably 0.02% or less. Since P and S in the flux lower toughness and cause cracking as impurities, the content is preferably limited to P: 0.02% or less and S: 0.01% or less.

Cr: 5.0 ~ 12%

Cr is an element that expands the ferrite region and at the same time forms Cr ₂ O ₃ to improve corrosion resistance. Since the content of Cr is related to the content of other flux elements, the content of Cr may vary slightly depending on the content of Ti, C and N. In the present invention, the content is set to 5.0-12%. In the case of Cr, it is possible to contain variously adjusted appropriately with the Cr content of the shell so that the Cr deficiency layer does not occur during welding of the material. As the content of Cr increases, the effect of corrosion resistance also increases, but when it exceeds 12%, not only the ductility decreases but also the content of Cr becomes excessively high. In this case, coarsening of crystal grains occurs in a heat-affected zone (HAZ) that rises to a temperature of 1100 ° C. or more, thereby causing a problem in that ductility and toughness are significantly reduced. On the other hand, Cr may be added in the form of Cr oxide or Cr alloy, wherein the Cr content should be converted into Cr conversion value.

Ni: 1.0 ~ 6.0%

Ni is an austenite stabilizing element, which has grain fineness and requires at least 1.0% to increase the ductility of the wire, but when it exceeds 6.0%, Ni reacts with Ni in the shell to increase its content, which saturates the effect, but the product cost itself Since it becomes expensive, its content is limited to 1.0-6.0%. Ni may be added in the form of Ni oxide or Ni alloy.

At least one of alkali oxides MgO, Na ₂ O, K ₂ O, CaO: 0.1 ~ 1.0%

Alkaline oxide acts as a slag generating agent and arc stabilizer, and its effect is low when the content is small, and when the content is high, the hygroscopic resistance is poor, and the smooth transition of the arc during welding is bad. In particular, Na and K have the effect of improving the spray transition state by reducing the volumetric displacement. If the content is high, it should not exceed 1.0% because it is easily generated by welding fume by evaporation during arc generation and the amount of spatter is also increased. . In addition, if it exceeds 1.0%, welding defects such as pits and blowholes may occur in the weld bead, which may adversely affect the welding bead.

Equation (1)

In the present invention, TiO ₂ , SiO ₂ and Al ₂ O were used as oxides, all of which serve as slag formers and arc stabilizers. In the present invention, the combination ratio (A) of the TiO ₂ and SiO ₂ , Al ₂ O ₃ and Mn is an important factor for the arc stability. Equation (1) must satisfy the range of 0.3 to 3.0. TiO ₂ is a slag forming agent and improves arc stability. It improves the appearance of beads after welding and improves the concentration of arcs, thereby suppressing spatter generation. However, when the content is increased, the amount of slag tends to increase, thereby decreasing the amount of welding per unit time (welding efficiency). SiO ₂ is a slag generating agent, and improves the flowability of the slag, when the content is large, there is a disadvantage that not only increases the amount of slag but also generates a large amount of spatter and welding fume, and decreases the workability of the slag. And in the case of Al ₂ O ₃ to control the slag flowability, and serves to improve the appearance of the bead appearance. However, if the content is high, there is a disadvantage in that toughness is reduced by remaining non-metallic inclusions in the deposited metal, so that the total amount is 0.1 to 3.0% by appropriately combining TiO ₂ , SiO ₂ , Al ₂ O ₃ oxides or including at least one kind. It is desirable to define.

Mn: 0.3 ~ 1.5%

Mn is an element that refines grains and is an austenite stabilizing element. In the present invention, Mn is added to sufficiently secure tensile strength. In particular, Mn also acts as a deoxidizer. In particular, it is preferable to define 0.3 to 1.5% because it forms an impurity P, S and a high melting point compound and a silicide to prevent high temperature cracking. However, in case of Mn, Mn fumes are generated, so the content should not be added too much. In particular, if Mn content is too high in the weld metal, there is a risk of grain boundary fracture, which leads to an increase in the crack initiation index K _IC . The content of Mn must satisfy the above-mentioned range and satisfy the combination ratio (A) according to Equation (1) to sufficiently secure the stability of the arc, so that the uniformity of arc transition can be maintained even at low current and low voltage. The effect of being reduced is shown.

In addition to the above-mentioned matters, other added irons include Si-based forms such as Fe-Si, and fluxes containing appropriate combinations of Mg and Al are used as arc stabilizers. The amount of oxygen in the weld metal can be minimized only when it is in the range of 0.1 to 10%, and internal defects such as pits and blue holes can be prevented.

The amount of flux filled in the hollow portion of the outer shell made of austenitic steel is not limited, but the amount of flux filled is preferably 10 to 20% as a percentage of the total weight of the wire. If the flux filling amount is less than 10%, the slag generation amount is insufficient to have all the features expected in the present invention. If the flux filling amount exceeds 20%, the wire is broken during the manufacturing process or bends during welding, which adversely affects the feedability. Because of giving.

Hereinafter, one embodiment of the present invention, but the present invention is not limited by the following examples.

Embodiments of the austenitic stainless steel metal cored wires in the present invention are shown in Tables 1, 2, 3, and 4.

Table 1 shows the welding conditions for the evaluation of welding workability. In order to make an accurate judgment, the conditions of 170-220A, 22-26V downward and 180-240A, 23-28V horizontally are used by using a 6mm thick SUS 304L steel sheet. Welding evaluation was performed. Regardless of the welding position, the welding speed was maintained at 35CPM, the shielding gas was 2% O ₂ + 98% Ar, and auto-carrier welding was performed to maintain the tip-base metal distance accurately. Welding conditions are shown in Table 1.

division Welding condition Grater STS 304L Base material thickness 6mm (t) Welding polarity DC (+) Shielding gas 2% O ₂ + 98Ar Gas supply amount Flow rate 20ℓ / min Welding position Downward Horizontal Fillet Welding current 170-220 180-240 Welding voltage 22-26 23-28 Welding speed 35 cm / min 35 cm / min Tip-Base Material Distance 20 mm 20 mm

Table 2 shows the composition ratio of the flux, and Table 3 shows the chemical composition of the deposited metal. In Table 2 (a) is TiO ₂ + SiO ₂ + Al ₂ O ₃ , (b) is the iron and arc stabilizer, (c) is the content of the alkali oxide.

Flux component (% by weight of wire total) (a) Cr Ni Mn Si (b) (c) C Combination Ratio (A) Comparative example Z1 0.055 6.380 2.894 0.360 0.083 1.372 0.011 <0.01 0.237 Z2 0.055 4.488 2.894 0.360 0.083 0.346 0.344 <0.01 0.118 Z3 0.449 6.938 3.832 1.653 0.100 1.372 1.879 <0.01 0.421 Z4 1.549 6.938 2.894 0.464 0.100 0.346 0.344 <0.01 3.501 Inventive Example Z5 0.178 6.380 2.894 0.499 0.083 0.132 0.122 <0.01 0.553 Z6 0.214 6.938 3.832 0.360 0.100 0.156 0.122 <0.01 0.921 Z7 0.449 8.375 3.233 0.800 0.125 0.346 0.344 <0.01 0.693 Z8 0.555 8.075 4.689 0.800 0.125 0.346 0.344 <0.01 0.796 Z9 1.540 6.380 2.894 0.800 0.083 0.132 0.344 <0.01 2.014 Z10 0.548 8.174 3.792 0.800 0.125 0.427 0.344 <0.01 0.789 Z11 1.222 6.380 2.894 0.499 0.125 0.132 0.122 <0.01 2.241 Z12 1.222 8.174 3.792 0.499 0.083 0.346 0.122 <0.01 2.672

Result of chemical composition analysis of weld metal (wt%) C P S Si Mn Cr Ni Comparative example Z1 0.032 0.015 0.008 0.037 1.18 24.61 11.14 Z2 0.036 0.018 0.007 0.040 1.23 21.35 12.31 Z3 0.028 0.020 0.009 0.053 1.74 23.97 12.54 Z4 0.030 0.024 0.005 0.044 1.34 23.23 12.11 Inventive Example Z5 0.030 0.023 0.009 0.044 1.41 23.14 12.80 Z6 0.028 0.015 0.012 0.048 1.25 23.81 12.44 Z7 0.029 0.018 0.014 0.037 1.25 23.14 12.14 Z8 0.034 0.018 0.008 0.054 1.55 24.78 13.10 Z9 0.028 0.020 0.009 0.48 1.43 22.78 12.77 Z10 0.030 0.024 0.015 0.34 1.26 22.80 12.30 Z11 0.033 0.024 0.012 0.40 1.37 23.11 11.99 Z12 0.029 0.018 0.005 0.42 1.41 24.53 12.20

Table 4 shows the comparative evaluation of the various properties of each wire manufactured as described above. In Table 4, ◎ is very good, O is good, △ is usually, X means bad.

sign Bead shape Volume size Arc stability slag generation spatter Combination Ratio (A) Comparative example Z1 △ X X △ X 0.237 Z2 X O X △ △ 0.118 Z3 △ O X △ X 0.421 Z4 △ △ △ X X 3.501 Inventive Example Z5 O △ △ O O 0.553 Z6 O △ △ O △ 0.921 Z7 △ O O O O 0.693 Z8 O △ O O △ 0.796 Z9 O O O △ O 2.014 Z10 O O ◎ ◎ O 0.789 Z11 O △ O △ △ 2.241 Z12 O △ △ △ O 2.672

The results of the workability and other welding properties of the comparative example and the inventive example of the present invention are shown in Tables 2, 3, and 4, and Z5 to Z12 of the inventive examples are based on the chemical composition constituting the flux within the range suggested by the present invention. The ratio between composition and chemicals is satisfactory, and the workability evaluation shows very good weldability even in the downward and horizontal fillets. In addition, the Cr and Ni content suitable for welding of the dissimilar metals on the welded metal chemistry is shown, and the arc is stable, the slag amount is low, and the amount of spatter is generated. And in the bead exterior part, it appears similar to many existing austenitic stainless steel welding materials.

On the other hand, in Comparative Examples Z1 to Z4, one or two kinds of chemical component analysis results constituting the flux are outside the range suggested by the present invention or outside the range of the formula (1) proposed by the present invention. There was a case where spatter generation was large due to poor or poor workability. In addition, when a large amount of slag forming agent is added, a large amount of slag having high hardness and poor peelability is formed on the surface of the weld metal, which causes inconvenience of having to perform slag detachment manually.

In the case of Comparative Example Z1, the content of TiO ₂ + SiO ₂ + Al ₂ O ₃ is less than 0.1% and the content of alkali oxide is added too little, resulting in repeated spraying and globular transfer. The flux stability outside the range of the combination ratio (A) resulted in poor arc stability during welding and high spatter generation during welding.

In the case of Comparative Example Z2 as well as Z1, the content of TiO ₂ + SiO ₂ + Al ₂ O ₃ was low, making it difficult to secure excellent arc stability, and also having a rough bead shape and low Cr content. It was difficult to secure. And the combination ratio (A) range was configured too low, the overall welding workability was bad.

In the case of Comparative Example Z3, the content of alkali oxide was 1.879%, so that smooth arc migration was not formed, spattering was somewhat generated, and the amount of welding (per minute) was decreased by increasing the relative slag amount. And the content of Mn in the weld metal was too high to increase the Mn content in the weld metal.

Comparative Example Z4 had no problem in terms of chemical composition, but the arc was somewhat unstable outside the above combination ratio (A) to ensure arc stability during welding. Occurred. In addition, the spray transfer form and the globular transfer form appear repeatedly during arc transfer, causing a large spatter.

On the other hand, the present invention also focused on securing excellent feedability to be suitable for automatic welding (Robot et al.) In terms of the welding method. The most important thing for improving supplyability is to secure the wire surface condition, the wire surface roughness and the hardness of the surface coating. The surface condition was improved in consideration of the fact that excellent supply properties were obtained when these were secured. In order to solve the work hardening problem that occurs during the primary drawing, heat treatment is performed at 1000 ℃ or higher, and after initial drawing, the initial 350 ± The heat treatment was performed at α ° C. for a long time to form Cr ₂ O ₃ having high hardness on the wire surface. However, although the hardness of the coating itself was high, the uniform coating was difficult due to the small fresh lubrication pool on the wire surface, especially the black color of the dry lubricant due to the use of shielding gases 2% O ₂ + 98% Ar and 100% Ar during welding. The formation of oxides caused problems to remain near the welds. In addition, when the flow rate of the fresh lubricant pool remaining on the wire surface is small, it is confirmed that the supplyability is unstable, and the wet lubricant is prepared for the second drawing by preparing the wire heat-treated at 1100 ° C or higher after the primary drawing. The wire surface oxide film was controlled by fresh using. The wire surface condition according to wet drawing satisfies the wire surface characteristics required by the present invention. As a result, it was possible to omit the 350 ° C heat treatment process after the second drawing, and as a result, it was possible to secure the excellent supplyability of the product. there was.

According to the present invention as described above, the metal cored wire for welding stainless steel of the present invention is the shielding gas used in many conventional stainless steel welding materials 100% CO ₂ to 100% Ar or 98% Ar + 2O ₂ It has been recognized for its excellence in environmentally friendly parts, and has improved the work efficiency by increasing the welding amount per unit time (welding efficiency) by using a lot of metal-based fluxes as well as stainless steel welding materials. By controlling the fresh lubrication pool generated, many existing stainless steel welding materials are used in the manufacturing process for degreasing the wire surface fresh lubricant and improving the supplyability of the product. Excellence in supplyability was secured even without the heat treatment). In other words, the effect of the present invention is highlighted in that the product productivity can be improved by reducing the overall reading time (Cycle time) of the manufacturing process.

Claims (2)

Metal cored wire for austenitic stainless steel welding, wherein the outer shell of the wire is made of low carbon stainless steel, and the flux filled in the outer shell is C: 0.02% or less, P: 0.02% or less, S: 0.01% or less, Cr: 5.0 to 12%, Ni: 1.0 to 6.0%, Mn: 0.3 to 1.5%, Si: 1.0% or less, at least one of alkali oxides MgO, Na ₂ O, K ₂ O, and CaO 0.1 to 1.0%, iron and arc stabilizers: 0.1 to 10%, oxides of TiO ₂ + SiO ₂ + Al ₂ O ₃ : 0.1 to 3.0%, but TiO ₂ , SiO ₂ , Al ₂ O ₃ and Mn are added The combination core (A) of following formula (1) satisfy | fills 0.3-3.0, The metal-cored wire for austenitic stainless steel welding characterized by the above-mentioned. Equation (1) The austenitic stainless steel welded metal cored wire is heat treated at 1100 ° C. or higher after primary drawing to perform secondary drawing, but the secondary drawing is drawn using a wet lubricant. Metal cored wire for stainless steel welding.