CN110142529B - Flux-cored wire for super duplex stainless steel gas shielded welding and preparation method thereof - Google Patents
Flux-cored wire for super duplex stainless steel gas shielded welding and preparation method thereof Download PDFInfo
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- CN110142529B CN110142529B CN201910359667.3A CN201910359667A CN110142529B CN 110142529 B CN110142529 B CN 110142529B CN 201910359667 A CN201910359667 A CN 201910359667A CN 110142529 B CN110142529 B CN 110142529B
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
- B23K35/308—Fe as the principal constituent with Cr as next major constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/40—Making wire or rods for soldering or welding
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Abstract
A flux-cored wire for gas shielded welding of super duplex stainless steel and a preparation method thereof. The flux-cored wire consists of an external steel belt and medicinal powder, wherein the external steel belt is an austenitic stainless steel belt with the chromium content of 17.0-18.0% and the nickel content of 11.0-12.5%; the medicinal powder comprises the following components in percentage by weight: 36.0-38.0 percent of chromium powder, 9.0-13.0 percent of high-nitrogen ferrochrome, 2.5-3.0 percent of electrolytic manganese metal, 4.0-5.0 percent of molybdenum powder, 0.5-1.0 percent of ferrosilicon, 1.0-1.5 percent of ferrotitanium, 0.5-1.0 percent of aluminum-magnesium alloy, 18.0-20.0 percent of rutile, 1.0-2.0 percent of quartz, 5.0-6.0 percent of zircon sand, 1.0-1.5 percent of potash feldspar, 3.0-3.5 percent of albite, 1.0-1.5 percent of fluorite, 0.5-1.0 percent of sodium cryolite, 1.0-1.5 percent of potassium titanate, 0.1-0.3 percent of bismuth oxide and the balance of iron powder. The invention can ensure the balance of the components and the proportion of two phases of the deposited metal and obtain the duplex stainless steel welding joint with good forming quality and excellent corrosion resistance.
Description
Technical Field
The invention relates to a flux-cored wire for gas shielded welding of super duplex stainless steel and a preparation method thereof, belonging to the field of welding of material processing engineering.
Background
The duplex stainless steel is a key special steel variety developed in the steel industry of China, and the ferrite phase and the austenite phase in the microstructure respectively account for 50 percent, so that the duplex stainless steel has the excellent toughness of the austenite stainless steel, also has the high strength and the chloride ion corrosion resistance of the ferrite stainless steel, and is increasingly widely applied to the fields of ocean structures, petrochemical industry, fresh water purification and the like.
Duplex stainless steel developed over three generations. The first generation duplex stainless steel is represented by 3RE60 steel developed in sweden in the middle of the 60 th 20 th century, which can be used in a chloride ion stress corrosion resistant environment, but the phase balance of a welded joint is extremely difficult to guarantee. The second generation duplex stainless steel is produced in the 70 th 20 th century, has the characteristics of ultralow carbon and nitrogen, and has the representative brand of SAF2205 and the pitting corrosion resistance index of 32-36. The third generation duplex stainless steel is super duplex stainless steel with ultralow carbon (less than or equal to 0.03%), high molybdenum (more than 3.5%) and high nitrogen (0.22-0.30%) which develops in the later 80 th of the 20 th century, has a pitting corrosion resistance index of more than 40, and is particularly suitable for serving in a marine corrosion environment.
Since the development of super duplex stainless steel, the super duplex stainless steel has excellent mechanical properties and high corrosion resistance, and has cost advantages compared with super austenitic stainless steel and nickel-based alloy materials with similar properties, and the application of the super duplex stainless steel in the fields with extremely harsh corrosion environments, such as marine structures, deep sea environments and other industries, is rapidly increased.
Welding is one of the key technologies applied to super duplex stainless steel, and the performance of a joint is a key factor influencing the overall safety of a stainless steel structure. The technical bottleneck of popularization and application of the super duplex stainless steel is that the corrosion resistance of a welding joint is not matched with that of a base metal, the welding joint is a weak link of a stainless steel welding structure, and the joint is corroded and damaged firstly in a corrosive environment, so that the whole structure is failed, the corrosion resistance of the super duplex stainless steel cannot be fully exerted, and a large amount of steel is wasted.
Literature data research shows that the molten or fused super duplex stainless steel base metal can be solidified and cooled to form a welding joint under the action of a welding heat source without adding welding materials in welding, but the austenite content of a welding seam is only about 30%, and the corrosion resistance of the welding seam is remarkably reduced; the content of austenite of weld metal can be improved by introducing nitrogen in the welding process, but because nitrogen comes from protective gas, the transition coefficient of the nitrogen depends on the ionization degree of the nitrogen in the welding process and the solubility of nitrogen elements in a welding pool, the nitrogen is greatly influenced by welding process parameters, and the chemical composition and the two-phase proportion of the weld metal are not easy to accurately control. Therefore, the welding of the super duplex stainless steel by using the special super duplex stainless steel phase welding material is the most effective measure for ensuring the corrosion resistance of the welding joint.
Disclosure of Invention
The invention aims to provide a flux-cored wire for gas shielded welding of super duplex stainless steel, which ensures the balance of two-phase proportions of austenite and ferrite in deposited metal by improving the chemical components and the composition of powder of an external steel strip of the flux-cored wire, thereby ensuring the corrosion resistance of a welding joint. On the basis, the invention can be further optimized to ensure that the welding wire has good welding process performance, thereby obtaining the super duplex stainless steel welding joint with good forming quality and excellent corrosion resistance.
The invention also aims to provide a preparation method of the flux-cored wire, because the content of alloy elements of the flux-cored wire for the gas shielded welding of the super duplex stainless steel is higher than that of the common stainless steel wire, the flux-cored wire with a fine diameter and high alloy content is manufactured by regulating and controlling the manufacturing process.
In order to achieve the purpose, the invention adopts the following technical scheme:
a flux-cored wire for super duplex stainless steel gas shielded welding comprises an external steel belt and powder, wherein the external steel belt is an austenitic stainless steel belt with 17.0-18.0% of chromium and 11.0-12.5% of nickel; the medicinal powder comprises the following components in percentage by weight: 36.0-38.0 percent of chromium powder, 9.0-13.0 percent of high-nitrogen ferrochrome, 2.5-3.0 percent of electrolytic manganese metal, 4.0-5.0 percent of molybdenum powder, 0.5-1.0 percent of ferrosilicon, 1.0-1.5 percent of ferrotitanium, 0.5-1.0 percent of aluminum-magnesium alloy, 18.0-20.0 percent of rutile, 1.0-2.0 percent of quartz, 5.0-6.0 percent of zircon sand, 1.0-1.5 percent of potash feldspar, 3.0-3.5 percent of albite, 1.0-1.5 percent of fluorite, 0.5-1.0 percent of sodium cryolite, 1.0-1.5 percent of potassium titanate, 0.1-0.3 percent of bismuth oxide and the balance of iron powder.
In the flux-cored wire, preferably, the content relationship between the chromium powder and the high-nitrogen ferrochrome in the medicinal powder satisfies 42.5-A + 0.6-B-45.5, wherein the chromium powder accounts for A% of the medicinal powder by weight, and the high-nitrogen ferrochrome accounts for B% of the medicinal powder by weight.
In the flux-cored wire as described above, preferably, the particle size distribution of the powder is: the medicinal powder with the granularity of 80-120 meshes accounts for 40-45 percent of the total weight of the medicinal powder; the medicinal powder with the granularity of 120-200 meshes accounts for 55-60% of the total weight of the medicinal powder.
In the flux-cored wire, the external steel band is preferably an austenite 316L stainless steel band, and the specification of the external steel band is as follows: the thickness is 0.4 plus or minus 0.02mm, and the width is 10 plus or minus 0.03 mm.
A preparation method of a flux-cored wire for super duplex stainless steel gas shielded welding comprises the following steps:
(1) sieving rutile, potassium feldspar and albite, controlling the particle size range within 80-150 meshes, and baking at 950 +/-10 ℃ for 60 +/-10 min;
(2) sieving quartz, zircon sand and potassium titanate, controlling the particle size range within 100-200 meshes, and baking at 500 +/-10 ℃ for 60 +/-10 min;
(3) sieving fluorite and sodium cryolite, controlling the particle size range within 120-200 meshes, and drying at 300 +/-10 ℃ for 60 +/-10 min;
(4) sieving the rest medicinal powder, wherein the granularity range is controlled within 80-200 meshes;
(5) all the medicinal powders are prepared in proportion, stirred and mixed uniformly and then dried for 60min +/-10 min at 120 +/-10 ℃;
(6) rolling the stainless steel belt into a U shape, and adding the powder of the medicine core after stirring and drying into the U-shaped groove;
(7) and after the U-shaped groove is closed, performing rolling forming and continuous drawing reducing treatment in sequence, and mechanically cleaning the surface of the welding wire to obtain a final product of the flux-cored wire.
The invention has the beneficial effects that:
the invention controls the chemical components and the two-phase ratio of the deposited metal of the flux-cored wire by controlling the contents of the alloy elements (mainly the contents of chromium, nickel and nitrogen) of the external steel strip and the powder of the flux-cored wire.
As for nickel element, the nickel content of the steel strip is reasonably controlled, so that the nickel element in the welding wire deposited metal is completely from the external stainless steel strip, the addition of nickel powder or nickel-containing substances in powder is avoided, the controllability of the nickel element content of the welding wire deposited metal is improved, and the powder filling coefficient required by welding wire manufacturing is reduced to reduce the difficulty of welding wire manufacturing, the external steel strip is preferably an austenitic stainless steel strip with the nickel content of 11.0-12.5%, and the nickel content of the welding wire deposited metal is preferably 9.0-10.5%.
As for nitrogen element, the nitrogen element is an important element of the super duplex stainless steel flux-cored wire, and the source of the nitrogen element is high-nitrogen ferrochrome in the welding wire powder. If the content of the high nitrogen ferrochrome in the powder is low, nitrogen is used as an austenitizing element, so that the content of austenite in a welding seam is too low, the corrosion resistance is reduced, and if the content of the high nitrogen ferrochrome in the powder is too high, air holes are generated in the welding seam, so that the welding quality is reduced. The content B% of high-nitrogen ferrochrome in the powder is preferably 9.0-13.0% so as to ensure that the nitrogen content of the deposited metal of the welding wire is preferably 0.20-0.30%.
After the nickel content in the preferable deposited metal, chromium is used as a ferrite element, and the content of the chromium in the deposited metal needs to be controlled so as to ensure the balance of two-phase ratio of austenite and ferrite in the deposited metal. In the case where the content of nickel element in the deposited metal is preferred, when the content of chromium is too high, the solid solution temperature of ferrite is lowered, which not only increases the high-temperature retention time of the weld pool and tends to cause coarsening of crystal grains, but also causes too low precipitation amount of austenite in the deposited metal due to precipitation of austenite in the weld pool at a low temperature, which is disadvantageous in securing the balance of the two-phase ratio. When the chromium content is too low, the strength of the deposited metal tends to be lowered. According to the invention, the welding wire is externally used with steel strips, chromium powder in the powder and high-nitrogen ferrochrome are used for transferring chromium elements to deposited metal, the chromium content of the external austenitic stainless steel strips is preferably 17.0-18.0%, and the content A% of the chromium powder in the powder is preferably 36.0-38.0%. Because the chromium content of the high-nitrogen ferrochrome is 60.0-65.0%, the invention also preferably controls A +0.6B within the range of 42.5-45.5 so as to ensure that the chromium content of the welding wire deposited metal is preferably 24.0-26.0%.
A certain amount of nitrogen is required in the deposited metal of the super duplex stainless steel flux-cored wire, and is usually not less than 0.2%. In order to ensure the nitrogen content in the deposited metal, the invention adds a proper amount of ferrotitanium into the powder, not only utilizes the strong deoxidation effect of the titanium element, but also utilizes the strong bonding force of the titanium element and the nitrogen element to improve the nitrogen fixation capability of the deposited metal. The content of ferrotitanium in the optimized powder is 1.0-1.5%, and when the content of ferrotitanium exceeds 1.5%, the welding process performance of the welding wire is deteriorated and welding spatter is increased.
In order to ensure the stability of welding manufacturability of the welding wire, the uniformity of powder filling needs to be controlled. The uniform filling of the medicinal powder is realized by controlling the apparent density of the medicinal powder and the volume of the cavity with a steel strip opening. When the powder granularity is smaller, the loose packing density of the powder is reduced, the fluidity is reduced, the required filling coefficient of the welding wire is increased, the filling is uneven, and the drawing and reducing of the welding wire are difficult; when the particle size of the medicinal powder is larger, the large-particle medicinal powder is easy to obstruct the subsequent filling of the medicinal powder, and the large-particle medicinal powder in the reducing process is difficult to compress and flow along with the large-particle medicinal powder, so that the phenomenon of thread breakage frequently occurs. The invention reasonably controls the granularity of each component in the medicinal powder, so that the coarse and fine particles of the mixed medicinal powder are matched with each other, and the loose packing density and the fluidity of the medicinal powder are increased to the maximum extent. The preferred particle size distribution of the medicinal powder is as follows: the medicinal powder with the granularity of 80-120 meshes accounts for 40-45 percent of the total weight of the medicinal powder; the medicinal powder with the granularity of 120-200 meshes accounts for 55-60% of the total weight of the medicinal powder. Correspondingly, the width and thickness deviation of the steel strip are important parameters influencing the volume of the cavity after the steel strip is closed, when the width or the thickness of the steel strip is too large or too small, the volume of the cavity after the steel strip is closed is large, and the medicinal powder in the drawing and reducing process is easy to move, so that the filling coefficient of the medicinal powder is fluctuated; when the width of the steel belt is too small or the thickness of the steel belt is too large, the volume of the cavity becomes small after the opening is closed, and asynchronous flowing of steel belt powder occurs in subsequent drawing and reducing, so that the phenomenon of rapid increase of the powder filling coefficient or wire breakage can be caused. The preferred dimensional tolerance of the external stainless steel band is the thickness +/-0.02 mm and the width +/-0.03 mm.
The acidity of the slag system of the flux-cored wire is properly reduced in the formula system of the flux-cored wire, so that the acidity of the slag system of the flux-cored wire is between a titanic acid type slag system and a neutral slag system, the flux-cored wire with excellent welding process performance is obtained, the welding seam forming quality is good, the metallurgical defects of pores, cracks, slag inclusion and the like are avoided, and the flux-cored wire can be used for 100 percent CO of super duplex stainless steel2And (4) carrying out gas shielded all-position welding.
Detailed Description
In the flux-cored wire for gas shielded welding of the super duplex stainless steel, the external steel strip of the flux-cored wire is an austenitic stainless steel strip with 17.0-18.0% of chromium and 11.0-12.5% of nickel, the specification of the flux-cored wire is 0.4 +/-0.02 mm in thickness and 10 +/-0.03 mm in width, and nickel elements, chromium elements and molybdenum elements are transited to surfacing welding.
The medicinal powder (medicine core powder) contains the following components in percentage by weight: 36.0-38.0 percent of chromium powder, 9.0-13.0 percent of high-nitrogen ferrochrome, 2.5-3.0 percent of electrolytic manganese metal, 4.0-5.0 percent of molybdenum powder, 0.5-1.0 percent of ferrosilicon, 1.0-1.5 percent of ferrotitanium, 0.5-1.0 percent of aluminum-magnesium alloy, 18.0-20.0 percent of rutile, 1.0-2.0 percent of quartz, 5.0-6.0 percent of zircon sand, 1.0-1.5 percent of potash feldspar, 3.0-3.5 percent of albite, 1.0-1.5 percent of fluorite, 0.5-1.0 percent of sodium cryolite, 1.0-1.5 percent of potassium titanate, 0.1-0.3 percent of bismuth oxide and the balance of iron powder. The powder preferably accounts for 22.0-23.0% of the total weight of the welding wire.
The welding wire powder comprises the following components in percentage by weight:
chromium powder: the content A percent (namely the weight percentage in the powder, the same below) of the transition chromium element in the welding wire deposited metal is 36.0 to 38.0 percent.
High nitrogen ferrochrome: the nitrogen content of the high-nitrogen ferrochrome is 10.0-12.0%, the chromium content is 60.0-65.0%, and chromium elements and nitrogen elements are transited to welding wire deposited metal. The content B% of the high nitrogen ferrochrome in the medicinal powder is 9.0-13.0%.
Moreover, the content of chromium powder and high-nitrogen ferrochrome in the medicinal powder preferably meets the following conditions: a is more than or equal to 42.5 and the B is more than or equal to 0.6 and less than or equal to 45.5.
Electrolyzing metal manganese: the manganese element is transited to the welding wire deposited metal, and the deoxidation and the desulfurization are performed, and the content of the manganese element is 2.5 to 3.0 percent.
Molybdenum powder: the content of transition molybdenum element in the welding wire deposited metal is 4.0-5.0%.
Silicon iron: the proper amount of transition silicon element is added into the deposited metal of the welding wire, and the transition silicon element and the manganese element are combined for slagging, and the content of the transition silicon element and the manganese element is 0.5 to 1.0 percent.
Titanium iron: mainly plays roles of deoxidation and nitrogen fixation, and the content of the nitrogen fixation agent is 1.0 to 1.5 percent.
Aluminum magnesium alloy: deoxidizing and participating in slag formation, wherein the content of the deoxidized slag formation is 0.5-1.0%.
Rutile: the main slag former can improve the slag detachability and the forming quality of weld metal, the welding bead slag shell can not be completely covered due to too little rutile, the protection effect of a molten pool is reduced, the slag detachability is reduced due to too much rutile, and the content of the slag detachability is 18.0-20.0% due to the air hole compression pit in the weld.
Quartz: the main slag former increases the acidity of the slag and adjusts the viscosity and the oxidability of the slag, but the excessive addition can increase the oxide inclusion amount in the deposited metal and reduce the weld forming quality, and the content of the slag former is 1.0-2.0%.
Zircon sand: the main slag former adjusts the physical and chemical properties of slag, improves the slag removal performance of weld metal, and improves the melting coefficient, and the content of the slag former is 5.0-6.0%.
Potassium feldspar: the slag forming agent is mainly used for slag forming and improving the stability of electric arc, and the content of the slag forming agent is 1.0-1.5%.
Albite: the slag forming agent is mainly used for slag forming, improves the welding arc stiffness and improves the all-position weldability, and the content of the slag forming agent is 3.0-3.5%.
Fluorite: dehydrogenation is carried out, and the air hole resistance of the weld metal is improved, wherein the content of the hydrogen is 1.0-1.5%.
Sodium cryolite: dehydrogenation is carried out, the fluidity of the slag is increased, the pore resistance of the weld metal is improved, and the content of the pore resistance is 0.5-1.0%.
Potassium titanate: stabilizing electric arc and participating in slag formation, and the content of the electric arc is 1.0-1.5%.
Bismuth oxide: improving the slag removal performance of the weld metal, and the content of the slag removal performance is 0.1-0.3%.
The balance being iron powder.
The preparation process of the flux-cored wire for the gas shielded welding of the super duplex stainless steel comprises the following steps:
the particle size range of rutile, potassium feldspar and albite in the medicinal powder is controlled to be 80-150 meshes, and high-temperature baking treatment is carried out at 950 +/-10 ℃ for 60 +/-10 min; controlling the particle size range of quartz, zircon sand and potassium titanate to be 100-200 meshes, and carrying out high-temperature baking treatment at 500 +/-10 ℃ for 60 +/-10 min; controlling the particle size range of fluorite and sodium cryolite within 120-200 meshes, and drying at 300 +/-10 ℃ for 60 +/-10 min; the particle size range of the rest of the medicinal powder is controlled to be 80-200 meshes; preparing all the medicinal powders according to a proportion, stirring and mixing uniformly, and drying at 120 +/-10 ℃ for 60 +/-10 min, wherein the particle size distribution of the final medicinal powder is as follows: the medicinal powder with the granularity of 80-120 meshes accounts for 40-45 percent of the total weight of the medicinal powder; the medicinal powder with the granularity of 120-200 meshes accounts for 55-60% of the total weight of the medicinal powder.
Rolling an austenitic stainless steel band with the specification of 0.4mm multiplied by 10mm into a U shape, and adding the flux-cored powder after stirring and drying into the U-shaped groove, wherein the flux-cored powder accounts for 22.0-23.0 percent of the total weight of the welding wire; and after the U-shaped groove is closed, performing rolling forming and continuous drawing reducing treatment in sequence, and mechanically cleaning the surface of the welding wire to obtain a final product of the flux-cored wire for the super duplex stainless steel gas shielded welding.
The present invention will be described in further detail with reference to the following examples, which are not intended to limit the present invention.
Example 1
Selecting an austenitic 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3347g, rolling the strip into a U shape, and adding 380g of chromium powder, 125g of high-nitrogen ferrochrome, 30g of electrolytic manganese metal, 50g of molybdenum powder, 10g of ferrosilicon, 15g of ferrotitanium, 10g of aluminum-magnesium alloy, 200g of rutile, 20g of quartz, 60g of zircon sand, 15g of potash feldspar, 35g of sodium feldspar, 15g of fluorite, 10g of sodium cryolite, 15g of potassium titanate, 3g of bismuth oxide and 7g of iron powder into 1000g of powder, wherein the granularity, the baking temperature and the baking time of each powder are shown in a table 2, uniformly mixing the powder, adding the powder into a U-shaped groove, the filling rate of 23.0 percent, and reducing the powder by multiple times after closing to finally obtain a finished welding wire with the diameter of phi 1.2 mm.
Example 2
Selecting an austenite 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3545g, rolling the stainless steel strip into a U shape, rolling 360g of chromium powder, 110g of high-nitrogen ferrochrome, 25g of electrolytic manganese metal, 40g of molybdenum powder, 5g of ferrosilicon, 10g of ferrotitanium, 5g of aluminum-magnesium alloy, 180g of rutile, 10g of quartz, 50g of zircon sand, 10g of potassium feldspar, 30g of sodium feldspar, 10g of fluorite, 5g of sodium cryolite, 10g of potassium titanate, 1g of bismuth oxide and 139g of iron powder into 1000g of medicinal powder, wherein the granularity, the baking temperature and the baking time of each medicinal powder are shown in a table 2, uniformly mixing the medicinal powder, adding the medicinal powder into a U-shaped groove, the filling rate of 22.0 percent, and reducing the diameter of the mixture by multiple passes after the mouth closing to finally obtain a finished welding.
Example 3
Selecting an austenitic 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3444g, rolling the stainless steel strip into a U shape, and adding 370g of chromium powder, 120g of high-nitrogen ferrochrome, 27g of electrolytic manganese metal, 45g of molybdenum powder, 7g of ferrosilicon, 12g of ferrotitanium, 8g of aluminum-magnesium alloy, 190g of rutile, 15g of quartz, 55g of zircon sand, 12g of potash feldspar, 33g of sodium feldspar, 12g of fluorite, 8g of sodium cryolite, 13g of potassium titanate, 2g of bismuth oxide and 71g of iron powder into 1000g of powder, wherein the granularity, the baking temperature and the baking time of each powder are shown in a table 2, uniformly mixing the powder, adding the powder into a U-shaped groove, the filling rate of 22.5 percent, and reducing the powder by multiple passes after closing, so as to finally obtain a finished welding wire with the diameter of.
Example 4
Selecting an austenite 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3545g, rolling the stainless steel strip into a U shape, rolling 380g of chromium powder, 90g of high-nitrogen ferrochrome, 30g of electrolytic manganese metal, 42g of molybdenum powder, 6g of ferrosilicon, 13g of ferrotitanium, 10g of aluminum-magnesium alloy, 195g of rutile, 18g of quartz, 58g of zircon sand, 12g of potash feldspar, 33g of sodium feldspar, 12g of fluorite, 10g of sodium cryolite, 15g of potassium titanate, 2g of bismuth oxide and 74g of iron powder, and totally 1000g of medicinal powder, wherein the granularity, the baking temperature and the baking time of each medicinal powder are shown in a table 2, uniformly mixing the medicinal powder, adding the medicinal powder into a U-shaped groove, the filling rate of 22.0 percent, and reducing the diameter of the mixture by multiple times to finally obtain a finished welding wire with.
Example 5
Selecting an austenitic 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3347g, rolling the strip into a U shape, rolling 360g of chromium powder, 130g of high-nitrogen ferrochrome, 26g of electrolytic manganese metal, 42g of molybdenum powder, 7g of ferrosilicon, 13g of ferrotitanium, 8g of aluminum-magnesium alloy, 185g of rutile, 12g of quartz, 55g of zircon sand, 13g of potash feldspar, 30g of sodium feldspar, 15g of fluorite, 5g of sodium cryolite, 15g of potassium titanate, 3g of bismuth oxide and 81g of iron powder, and obtaining 1000g of medicinal powder in total, wherein the granularity, the baking temperature and the baking time of each medicinal powder are shown in a table 2, uniformly mixing the medicinal powder, adding the medicinal powder into a U-shaped groove, the filling rate of 23.0%, and performing multi-pass diameter reduction after closing to finally obtain a finished welding wire with the diameter.
Comparative example 1
Selecting an austenite 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3545g, rolling the stainless steel strip into a U shape, rolling 420g of chromium powder, 110g of high-nitrogen ferrochrome, 25g of electrolytic manganese metal, 40g of molybdenum powder, 5g of ferrosilicon, 10g of ferrotitanium, 5g of aluminum-magnesium alloy, 180g of rutile, 10g of quartz, 50g of zircon sand, 10g of potassium feldspar, 30g of sodium feldspar, 10g of fluorite, 5g of sodium cryolite, 10g of potassium titanate, 1g of bismuth oxide and 79g of iron powder into 1000g of medicinal powder, wherein the granularity, the baking temperature and the baking time of each medicinal powder are shown in a table 2, uniformly mixing the medicinal powder, adding the medicinal powder into a U-shaped groove, the filling rate of 22.0 percent, and reducing the diameter of the mixture by multiple passes after the mouth closing to finally obtain a finished welding.
Comparative example 2
Selecting an austenite 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3545g, rolling the stainless steel strip into a U shape, rolling 380g of chromium powder, 150g of high-nitrogen ferrochrome, 30g of electrolytic manganese metal, 42g of molybdenum powder, 6g of ferrosilicon, 15g of ferrotitanium, 10g of aluminum-magnesium alloy, 195g of rutile, 18g of quartz, 58g of zircon sand, 12g of potash feldspar, 33g of sodium feldspar, 12g of fluorite, 10g of sodium cryolite, 15g of potassium titanate, 2g of bismuth oxide and 12g of iron powder, and totally 1000g of medicinal powder, wherein the granularity, the baking temperature and the baking time of each medicinal powder are shown in a table 2, uniformly mixing the medicinal powder, adding the medicinal powder into a U-shaped groove, the filling rate of 22.0 percent, and reducing the diameter of the mixture by multiple times to finally obtain a finished welding wire with.
Comparative example 3
Selecting an austenitic 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3444g, rolling the stainless steel strip into a U shape, and adding 370g of chromium powder, 120g of high-nitrogen ferrochrome, 27g of electrolytic manganese metal, 45g of molybdenum powder, 7g of ferrosilicon, 5g of ferrotitanium, 8g of aluminum-magnesium alloy, 190g of rutile, 15g of quartz, 55g of zircon sand, 12g of potash feldspar, 33g of sodium feldspar, 12g of fluorite, 8g of sodium cryolite, 13g of potassium titanate, 2g of bismuth oxide and 78g of iron powder into 1000g of powder, wherein the granularity, the baking temperature and the baking time of each powder are shown in a table 2, uniformly mixing the powder, adding the powder into a U-shaped groove, the filling rate of 22.5 percent, and reducing the powder by multiple passes after closing, so as to finally obtain a finished welding wire with the diameter of.
Comparative example 4
Selecting an austenitic 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3347g, rolling the strip into a U shape, rolling 360g of chromium powder, 130g of high-nitrogen ferrochrome, 26g of electrolytic manganese metal, 42g of molybdenum powder, 7g of ferrosilicon, 13g of ferrotitanium, 8g of aluminum-magnesium alloy, 185g of rutile, 12g of quartz, 55g of zircon sand, 13g of potash feldspar, 30g of sodium feldspar, 15g of fluorite, 5g of sodium cryolite, 15g of potassium titanate, 3g of bismuth oxide and 81g of iron powder, and obtaining 1000g of medicinal powder in total, wherein the granularity, the baking temperature and the baking time of each medicinal powder are shown in a table 2, uniformly mixing the medicinal powder, adding the medicinal powder into a U-shaped groove, the filling rate of 23.0%, and performing multi-pass diameter reduction after closing to finally obtain a finished welding wire with the diameter.
Comparative example 5
Selecting an austenitic 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3347g, rolling the strip into a U shape, rolling 360g of chromium powder, 130g of high-nitrogen ferrochrome, 26g of electrolytic manganese metal, 42g of molybdenum powder, 7g of ferrosilicon, 13g of ferrotitanium, 8g of aluminum-magnesium alloy, 185g of rutile, 12g of quartz, 55g of zircon sand, 13g of potash feldspar, 30g of sodium feldspar, 15g of fluorite, 5g of sodium cryolite, 15g of potassium titanate, 3g of bismuth oxide and 81g of iron powder, and obtaining 1000g of medicinal powder in total, wherein the granularity, the baking temperature and the baking time of each medicinal powder are shown in a table 2, uniformly mixing the medicinal powder, adding the medicinal powder into a U-shaped groove, the filling rate of 23.0%, and performing multi-pass diameter reduction after closing to finally obtain a finished welding wire with the diameter.
Comparative example 6
Selecting an austenitic 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3347g, rolling the strip into a U shape, and adding 380g of chromium powder, 125g of high-nitrogen ferrochrome, 30g of electrolytic manganese metal, 50g of molybdenum powder, 10g of ferrosilicon, 15g of ferrotitanium, 10g of aluminum-magnesium alloy, 200g of rutile, 20g of quartz, 60g of zircon sand, 15g of potash feldspar, 35g of sodium feldspar, 15g of fluorite, 10g of sodium cryolite, 15g of potassium titanate, 3g of bismuth oxide and 7g of iron powder into 1000g of powder, wherein the granularity, the baking temperature and the baking time of each powder are shown in a table 2, uniformly mixing the powder, adding the powder into a U-shaped groove, the filling rate of 23.0 percent, and reducing the powder by multiple times after closing to finally obtain a finished welding wire with the diameter of phi 1.6 mm.
Comparative example 7
Selecting an austenite 316L stainless steel strip (the main components and specifications are shown in a table 1) with the thickness of 0.4mm, the width of 10mm and the weight of 3545g, rolling the stainless steel strip into a U shape, rolling 360g of chromium powder, 110g of high-nitrogen ferrochrome, 25g of electrolytic manganese metal, 40g of molybdenum powder, 5g of ferrosilicon, 10g of ferrotitanium, 5g of aluminum-magnesium alloy, 280g of rutile, 10g of quartz, 50g of zircon sand, 10g of potassium feldspar, 30g of sodium feldspar, 10g of fluorite, 5g of sodium cryolite, 10g of potassium titanate, 1g of bismuth oxide and 39g of iron powder, and obtaining 1000g of medicinal powder in total, wherein the granularity, the baking temperature and the baking time of each medicinal powder are shown in a table 2, uniformly mixing the medicinal powder, adding the medicinal powder into a U-shaped groove, the filling rate of 22.0 percent, and reducing the diameter of the finished welding wire with the diameter of 1.2.
TABLE 1 practical technical parameters of the steel strips for external use of examples and comparative examples
TABLE 2 particle size, baking/stoving temperature and time for each component of the powders of the examples and comparative examples
Evaluation of the properties of the examples and comparative examples:
with 100% CO2The flux-cored wire for welding the examples and the comparative examples of the gas shielded welding has the following welding process parameters: welding current 180A, welding voltage 27V, welding speed 20cm/min, gas flow 20L/min, and preparing the welding wire deposited metal according to the method in GB/T17853 stainless steel flux-cored wire. Welding manufacturability by using GB/T25776 welding materialThe welding process performance of the welding wire can be evaluated by an evaluation method, a FISCHER ferrite determinator MP30 is adopted to test the ferrite content of the cross section of the welding line, each welding line is tested for five times, and the average value is taken.
The effect ratios of the examples and comparative examples are shown in table 3.
As can be seen from the results in Table 3, in comparative example 1 in which the amount of chromium powder added in the powder exceeded 38.0% and the weight percentage of chromium powder and high nitrogen ferrochrome A +0.6B in the powder was more than 45.5, the content of chromium element in the deposited metal was high, the chromium-nickel ratio was large, and the ferrite content in the structure reached 65.4%, which resulted in the deterioration of corrosion resistance. For the comparative example 2 with the high nitrogen ferrochrome content in the powder exceeding 13.0 percent, the nitrogen content in the powder is too high, nitrogen elements are difficult to be completely dissolved in weld deposit metal, and a nitrogen hole is generated in a weld, so that the welding quality is reduced. For the comparative example 3 with the ferrotitanium content of less than 1.0 percent in the powder, the titanium element plays roles of deoxidation and nitrogen fixation in the welding process, and the reduction of the content of the titanium element causes the reduction of the content of nitrogen element in deposited metal, the reduction of the content of austenite in a structure, and the increase of the content of ferrite, which are not beneficial to ensuring the corrosion resistance. For comparative example 4 in which the nickel content in the steel strip was less than 11.0%, the nickel content in the welding wire deposited metal was low, the austenite content in the structure was reduced, the ferrite content was increased, and the corrosion resistance was decreased. For the comparative example 5 that the width of the external steel strip exceeds 10.03mm, the volume of a cavity formed after the steel strip is jointed is increased, and the powder is easy to move in the cavity, so that the powder filling coefficient is fluctuated, the welding arc is unstable, the welding spatter is increased, and the welding process performance of the welding wire is deteriorated. For comparative example 6 in which the powder was not baked as required, the mineral powder contained much water of combination, crystal water, and adsorbed water, and the water content in the powder was too high, which resulted in unstable welding arc during welding and easily caused blowholes in the weld; the secondary powder is not subjected to granularity control according to requirements, the particle size is not uniform, the drawing and reducing difficulty is increased by coarse particles, the fluidity is reduced by fine particles, the powder filling is not uniform, the arc stability is reduced, and the welding process performance is deteriorated. For comparative example 7 in which the content of rutile in the powder exceeds 22.0%, the slag-forming constituent in the powder is too much, the melting point of the skull rises, the skull solidifies first during cooling, the welding pool cannot flow freely because of the limitation of the solidified skull, the forming quality of the weld surface is deteriorated, the slag-off rate is reduced, and in addition, oxide inclusions are easily generated in the deposited metal, which results in the reduction of the corrosion resistance.
The flux-cored wire prepared in the embodiments 1 to 6 has good welding manufacturability, low welding seam blowhole tendency, moderate ferrite content of welding wire deposited metal, and obviously better comprehensive performance than that of the comparative examples 1 to 7, and can be used for gas shielded welding of super duplex stainless steel (such as SUS 2507).
TABLE 3 evaluation of the wire Properties of examples and comparative examples
Claims (6)
1. A flux-cored welding wire for super duplex stainless steel gas shielded welding consists of an external steel belt and powder, and is characterized in that the powder accounts for 22.0-23.0% of the total weight of the welding wire; the external steel belt is an austenitic stainless steel belt with the chromium content of 17.0-18.0% and the nickel content of 11.0-12.5%; the medicinal powder comprises the following components in percentage by weight: 36.0-38.0 percent of chromium powder, 9.0-13.0 percent of high-nitrogen ferrochrome, 2.5-3.0 percent of electrolytic manganese metal, 4.0-5.0 percent of molybdenum powder, 0.5-1.0 percent of ferrosilicon, 1.0-1.5 percent of ferrotitanium, 0.5-1.0 percent of aluminum-magnesium alloy, 18.0-20.0 percent of rutile, 1.0-2.0 percent of quartz, 5.0-6.0 percent of zircon sand, 1.0-1.5 percent of potash feldspar, 3.0-3.5 percent of albite, 1.0-1.5 percent of fluorite, 0.5-1.0 percent of sodium cryolite, 1.0-1.5 percent of potassium titanate, 0.1-0.3 percent of bismuth oxide and the balance of iron powder.
2. The flux-cored wire of claim 1, wherein the content relationship between the chromium powder and the high-nitrogen ferrochrome in the powder satisfies 42.5-A + 0.6-B-45.5, wherein the chromium powder accounts for A% of the powder by weight, and the high-nitrogen ferrochrome accounts for B% of the powder by weight.
3. The flux-cored welding wire of claim 1, wherein the powder has a particle size distribution of: the medicinal powder with the granularity of 80-120 meshes accounts for 40-45 percent of the total weight of the medicinal powder; the medicinal powder with the granularity of 120-200 meshes accounts for 55-60% of the total weight of the medicinal powder.
4. The flux cored welding wire of claim 1, wherein the outer steel band is an austenitic 316L stainless steel band.
5. The flux-cored welding wire of claim 1, wherein the external steel strip has the following specifications: the thickness is 0.4 plus or minus 0.02mm, and the width is 10 plus or minus 0.03 mm.
6. A method of making a flux-cored welding wire of any one of claims 1 to 5, comprising the steps of:
(1) sieving rutile, potassium feldspar and albite, controlling the particle size range within 80-150 meshes, and baking at 950 +/-10 ℃ for 60 +/-10 min;
(2) sieving quartz, zircon sand and potassium titanate, controlling the particle size range within 100-200 meshes, and baking at 500 +/-10 ℃ for 60 +/-10 min;
(3) sieving fluorite and sodium cryolite, controlling the particle size range within 120-200 meshes, and drying at 300 +/-10 ℃ for 60 +/-10 min;
(4) sieving the rest medicinal powder, wherein the granularity range is controlled within 80-200 meshes;
(5) all the medicinal powders are prepared in proportion, stirred and mixed uniformly and then dried for 60min +/-10 min at 120 +/-10 ℃;
(6) rolling the stainless steel belt into a U shape, and adding the powder of the medicine core after stirring and drying into the U-shaped groove;
(7) and after the U-shaped groove is closed, performing rolling forming and continuous drawing reducing treatment in sequence, and mechanically cleaning the surface of the welding wire to obtain a final product of the flux-cored wire.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1686661A (en) * | 2005-06-10 | 2005-10-26 | 北京工业大学 | Pile up welding cored electrode for shield tool bit cutting edge |
| CN102229029A (en) * | 2011-05-30 | 2011-11-02 | 中冶焊接科技有限公司 | Flux-cored wire for austenitic stainless steel all-position welding |
| CN103521951A (en) * | 2013-11-04 | 2014-01-22 | 北京金威焊材有限公司 | Flux-cored wire for stainless steel welding |
| CN106077992A (en) * | 2016-07-07 | 2016-11-09 | 南京航空航天大学 | A kind of mould electric arc that is applicable to increases micro-slag gas-shielded flux-cored wire that material manufactures |
| CN107931887A (en) * | 2017-11-16 | 2018-04-20 | 天津大桥焊材集团有限公司 | A kind of end socket special stainless steel gas shielded arc welding flux-cored wire and preparation method thereof |
| JP2018192520A (en) * | 2017-05-22 | 2018-12-06 | 新日鐵住金株式会社 | Flux-cored wire for gas shield arc welding, and manufacturing method of weld joint |
-
2019
- 2019-04-29 CN CN201910359667.3A patent/CN110142529B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1686661A (en) * | 2005-06-10 | 2005-10-26 | 北京工业大学 | Pile up welding cored electrode for shield tool bit cutting edge |
| CN102229029A (en) * | 2011-05-30 | 2011-11-02 | 中冶焊接科技有限公司 | Flux-cored wire for austenitic stainless steel all-position welding |
| CN103521951A (en) * | 2013-11-04 | 2014-01-22 | 北京金威焊材有限公司 | Flux-cored wire for stainless steel welding |
| CN106077992A (en) * | 2016-07-07 | 2016-11-09 | 南京航空航天大学 | A kind of mould electric arc that is applicable to increases micro-slag gas-shielded flux-cored wire that material manufactures |
| JP2018192520A (en) * | 2017-05-22 | 2018-12-06 | 新日鐵住金株式会社 | Flux-cored wire for gas shield arc welding, and manufacturing method of weld joint |
| CN107931887A (en) * | 2017-11-16 | 2018-04-20 | 天津大桥焊材集团有限公司 | A kind of end socket special stainless steel gas shielded arc welding flux-cored wire and preparation method thereof |
Non-Patent Citations (2)
| Title |
|---|
| 一种不锈钢水轮机用堆焊药芯焊丝的研制;王磊等;《焊接技术》;20130930;第42卷(第9期);第59-63页 * |
| 双相不锈钢药芯焊丝;乜枫展等;《机械制造文摘(焊接分册)》;20121031(第05期);第34-36页 * |
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