CN115780967A - Bottom layer welding process for ZGMn13Mo high manganese steel and A514 low alloy steel - Google Patents
Bottom layer welding process for ZGMn13Mo high manganese steel and A514 low alloy steel Download PDFInfo
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- CN115780967A CN115780967A CN202211597562.XA CN202211597562A CN115780967A CN 115780967 A CN115780967 A CN 115780967A CN 202211597562 A CN202211597562 A CN 202211597562A CN 115780967 A CN115780967 A CN 115780967A
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Abstract
The invention discloses a priming layer welding process for ZGMn13Mo high manganese steel and A514 low alloy steel, which is suitable for the technical field of dissimilar steel welding. Aiming at the problem of common welding cracks of ZGMn13Mo high manganese steel and A514 low alloy steel dissimilar steel in the welding process, the process obtains proper heat input and improves the appearance of a welding seam by changing the welding current under the premise of ensuring that the welding current and the welding speed are not changed by adopting a gas metal arc welding method, and realizes that the continuity and the uniformity of the welding seam are good and no obvious macroscopic welding crack defect exists in the GMAW welding process of 25mm thick ZGMn13Mo high manganese steel and A514 low alloy steel in a priming layer. The welding process can improve the weld forming quality and obviously improve the quality of the dissimilar steel welding joint of ZGMn13Mo high manganese steel and A514 low alloy steel. The method has important significance for promoting the practical engineering application and development of the welding of ZGMn13Mo high manganese steel and A514 low alloy steel dissimilar steel.
Description
Technical Field
The invention provides a priming coat welding process for ZGMn13Mo high manganese steel and A514 low alloy steel, belongs to the technical field of dissimilar steel welding, and is suitable for improving the main problems of welding cracks and the like generated in the process of welding the priming coat of the high manganese steel and the low alloy steel.
Background
ZGMn13Mo high manganese steel is wear-resistant steel, has high tensile strength, plasticity, toughness, wear resistance and good comprehensive mechanical property, can bear larger impact load without breaking even if the material is worn to be thin and parts are worn to be thin, can be used for manufacturing various impact-resistant wearing parts, such as shovel teeth of an excavator, rolling surface walls and crushing walls of a cone crusher, fork plates of a jaw crusher, lining plates of a ball mill, railway frogs, plate hammers, hammer heads and the like, and is an important material which is used in the fields of transportation, metallurgy mines and the like in a large quantity. The A514 steel is a high-strength weldable steel plate subjected to quenching and tempering under an ASTM standard, can be divided into eight grades, is mainly used in places needing high tensile strength and high yield, such as lifting gears of engineering automobiles, racks for ocean platforms, buckets of electric shovel buckets and the like, has the general mechanical properties similar to that of Q690 in China, and has high tensile strength and high yield strength.
The linear expansion coefficient of ZGMn13Mo high manganese steel is 1.6 times of that of low carbon steel, but the thermal conductivity is only 1/6 of that of the low carbon steel, so that great stress can be generated during welding, and under the action of S, P harmful impurities, weld heat cracks and liquefaction cracks of a heat affected zone are easily generated. A514 steel adds a plurality of alloy elements for improving hardenability due to the alloying principle, thereby leading to larger hardenability tendency and great cold cracking tendency. For dissimilar steel welding, due to the obvious difference of the thermal expansion coefficient, the thermal conductivity coefficient and other properties between base metals and between the base metals and the filling materials, larger welding stress is generated in the welding process, and the crack tendency is further increased. Such dissimilar steels often exhibit through-growth macro weld cracking in actual component applications.
Aiming at the problems, gas metal arc welding is adopted, and compared with the traditional tungsten electrode argon arc welding, the gas metal arc welding has the characteristics of concentrated heat source and small linear energy, and is favorable for inhibiting the generation of cracks. For the welding of ZGMn13Mo high manganese steel and A514 low alloy steel same kind steel, the mature welding process improves the welding defects of welding cracks, joint softening and the like in the welding process at present. However, the dissimilar steel welding research foundation of ZGMn13Mo high manganese steel and A514 low alloy steel is weak, and a systematic welding process improvement scheme is not formed yet.
At present, the problem of welding cracks generated by welding dissimilar steel of ZGMn13Mo high manganese steel and A514 low alloy steel is not well solved, and the application development of the ZGMn13Mo high manganese steel and the A514 low alloy steel in a welding structure is restricted to a certain extent.
Disclosure of Invention
In view of the limitation of the background technology, the invention provides a priming layer welding process for ZGMn13Mo high manganese steel and A514 low alloy steel, which does not need complex external tools, adopts Cr-Ni austenitic steel welding wire with the mark of ER309LT1-1, obviously improves the problem of welding cracks generated by welding the priming layer of the ZGMn13Mo high manganese steel and the A514 low alloy steel by adjusting the welding process parameters, obtains continuous and uniform weld forming, and can provide reference for GMAW welding of the ZGMn13Mo high manganese steel and the A514 low alloy steel.
The technical scheme of the invention is as follows:
a base material adopts a ZGMn13Mo high manganese steel and A514 low alloy steel thick plate with the thickness of 25mm, the groove is 60 degrees, and a butt joint mode is adopted; adopting an ER309LT 1-flux-cored wire with the diameter of 1.6mm as a filling material; adopting a gas metal arc welding method, wherein the welding current is 180-240A, the welding voltage is 24V, and the welding speed is 40cm/min; adopts 82 percent of Ar +18 percent 2 As the shielding gas, the flow rate was 25L/min.
Furthermore, the adopted welding equipment is a gas metal arc welding system which mainly comprises a loose TA-1400 welding robot, a loose TRANS-30 power supply and a loose YD-ABD35 robot control cabinet.
Further, the welding voltage and the welding speed are kept unchanged in the welding process, and the influence of different welding currents on the weld forming is researched.
And further, after welding is finished, carrying out sample preparation and shooting on the weld macroscopic forming and the cross section metallographic morphology.
The beneficial effects of the invention are as follows: by adopting the filling material with better plastic toughness and moderate heat input, the high-temperature retention time of the ZGMn13Mo high manganese steel side can be reduced, the precipitation of carbide is reduced, the initiation of hot cracks is avoided, the increase of the quenching tendency of the A514 low alloy steel side caused by too high cooling speed can also be avoided, the generation of cold cracks is inhibited, meanwhile, the stress of a dissimilar steel welding joint can also be reduced, and then the continuous and uniform welding seam forming without the defects of welding cracks and the like is obtained, and the welding quality is improved.
Drawings
FIG. 1 is a GMAW welding schematic diagram of ZGMn13Mo high manganese steel and A514 low alloy steel.
FIG. 2 is the macro topography of the weld surface of examples 1-4.
FIG. 3 is the cross-sectional macro metallographic morphology of the weld joints of examples 1 to 4.
FIG. 4 is the cross-sectional microscopic metallographic morphology of the weld of examples 1-4.
Detailed Description
The present invention is further illustrated by the following examples.
Example 1
Adopting ZGMn13Mo high manganese steel with the thickness of 25mm and an A514 low alloy steel thick plate as welding parent metals, processing the specification of a sample to 100mm multiplied by 50mm multiplied by 25mm through linear cutting, having no truncated edge, reserving a 2mm gap, and welding in a flat plate butt joint mode; before welding, the surface of the base material is mechanically cleaned, the surface is carefully inspected for the presence of defects such as cracks, pores and shrinkage cavities, and if the defects are present, the surface of the base material needs to be shoveled out by a grinding wheel or an arc gouging and wiped by an alcohol reagent to remove impurities such as rust and oil stains on the surface. And in the welding process, clamping and fixing the test plate by using a tool clamp.
And impurities such as oil stains. In the welding process, a test plate is clamped and fixed by a tool clamp.
Welding ofA loose welding robot is adopted, the welding current is 180A, the welding voltage is 24V, and the welding speed is 40cm/min; protection gas is 82% Ar +18% CO 2 The flow rate was 25L/min.
And shooting the formed weld surface after welding, preparing a weld metallographic sample through the processes of electric spark cutting, grinding, polishing, corroding and the like, and shooting the metallographic appearance of the cross section.
Example 2
The size, type and surface treatment before welding of the base material are the same as those of the embodiment 1, the welding adopts a loose welding robot, the welding current is 200A, the welding voltage is 24V, and the welding speed is 40cm/min; protection gas is 82% Ar +18% CO 2 The flow rate was 25L/min.
And shooting the formed weld surface after welding, preparing a weld metallographic sample through the processes of electric spark cutting, embedding, grinding, polishing, corroding and the like, and shooting the metallographic appearance of the cross section.
Example 3
The size, type and surface treatment before welding of the base material are the same as those of the embodiment 1, the welding adopts a loose welding robot, the welding current is 220A, the welding voltage is 24V, and the welding speed is 40cm/min; protection gas is 82% Ar +18% CO 2 The flow rate was 25L/min.
And shooting the formed surface of the welding seam after welding, preparing a welding seam metallographic specimen through the processes of electric spark cutting, embedding, grinding, polishing, corrosion and the like, and shooting the metallographic appearance of the cross section.
Example 4
The size, type and surface treatment before welding of the base material are the same as those of the embodiment 1, the welding adopts a loose welding robot, the welding current is 240A, the welding voltage is 24V, and the welding speed is 40cm/min; protection gas is 82% Ar +18% CO 2 The flow rate was 25L/min.
And shooting the formed surface of the welding seam after welding, preparing a welding seam metallographic specimen through the processes of electric spark cutting, embedding, grinding, polishing, corrosion and the like, and shooting the metallographic appearance of the cross section.
The weld surface formation obtained in examples 1 to 4 is shown in fig. 2, the macroscopic metallographic morphology of the cross section of the weld is shown in fig. 3, and the microscopic metallographic morphology of the cross section of the weld is shown in fig. 4. It can be seen that by properly increasing the welding current, the heat input is continuously increased, the weld surface is formed more continuously and uniformly, and no macroscopic welding cracks appear, but the further increase of the welding current can cause the arc instability in the welding process, and the protective gas flow is disturbed, so that the welding bead is blown off. In addition, in the welding process, the filler metal reflows to the middle position of the welding seam due to the restraint of the welding parent metal at two sides, so that the metal at the center position of the welding seam is extruded to present a straight line shape. From the macroscopic metallographic morphology of the cross section of the welding seam, the filling metal and the welding base metal are well fused, the fusion line is clear and obvious, and no welding crack is found at the welding seam and the heat affected zone. In addition, the weld penetration and the weld width are increased successively with the increase of the welding current, but the weld penetration and the weld width change are small in other examples except the example 1, and the increase of the heat input causes the width of a ZGMn13Mo high manganese steel side Heat Affected Zone (HAZ) to be obviously increased, but the width of an A514 low alloy steel side heat affected zone is not obviously changed. Meanwhile, due to the fact that clamping is not firm, the problems of misalignment, small gaps and the like occur in the welding process, and further the defects of slag inclusion, air holes and the like occur, and the problems are avoided in actual operation. From the microscopic metallographic morphology of the cross section of the welding seam, no crack is found in the center of the welding seam, a fusion line and heat affected zones on two sides under a fifty-fold microscope lens; the central structure of the welding seam is dense columnar crystal and becomes coarse along with the increase of heat input, the ZGMn13Mo high manganese steel side base material is austenite (A), the coarsening degree of the heat affected zone structure is increased due to the increase of the heat input, and the sensitivity of heat cracks is further increased, the A514 low alloy steel side base material is ferrite (F), the structure close to the welding seam heat affected zone is martensite (M) and a small amount of bainite (B), the structure is coarse along with the formation of martensite and residual austenite (M + A) due to the increase of the heat input, the brittle phase of the M + A structure is easy to cause stress concentration at the grain boundary, cold cracks are initiated at the grain boundary, and therefore, the excessive heat input is avoided. The macroscopic morphology and the microscopic metallographic morphology of the welding seam are combined to discover that the welding seam is discontinuous and poor in forming under the condition that the welding current is 180A, the welding seam M + A is increased under the condition that the welding current is 240A, the structure coarsening is serious, the crack sensitivity is increased, the evenness and the continuity of the welding seam of the bottoming layer are good under the condition that the welding current is 200A and 220A, the welding seam has no welding seam blow, the tendency of the welding seam structure crack is relatively small, and the welding crack is not easy to initiate.
The analysis of the results of the embodiment shows that the bottoming layer welding process of the ZGMn13Mo high manganese steel and the A514 low alloy steel can avoid the problem of welding cracks in the GMAW welding process of the ZGMn13Mo high manganese steel and the A514 low alloy steel by changing the welding current to obtain proper heat input, form continuous and uniform welding seams without macroscopic welding cracks, and remarkably improve the quality of welding joints of dissimilar steels. The method has important significance for promoting the practical engineering application and development of the welding of ZGMn13Mo high manganese steel and A514 low alloy steel dissimilar steel.
The foregoing is only a few embodiments of the present invention, which is not intended to be limiting in any way. Any simple modification, equivalent replacement, and improvement made to the above embodiments by those skilled in the art without departing from the technical scope of the present invention still fall within the protection scope of the claims of the present invention.
Claims (2)
1. A primer layer welding process for ZGMn13Mo high manganese steel and A514 low alloy steel is characterized by comprising the following steps: the welding parent metal is ZGMn13Mo high manganese steel and A514 low alloy steel thick plate with the thickness of 25mm, the bevel is 60 degrees, and a butt joint mode is adopted; adopting an ER309LT1-1 flux-cored wire with the diameter of 1.6mm as a filling material; adopting a welding method of gas metal arc welding, wherein the welding current is 200-220A, the welding voltage is 24V, and the welding speed is 40cm/min; using 82% of Ar +18% 2 As the shielding gas, the flow rate was 25L/min.
2. The process of claim 1 for primer layer welding of ZGMn13Mo high manganese steel with a514 low alloy steel, wherein: the welding method of gas metal arc welding is adopted, ER309LT1-1 flux-cored wire with the diameter of 1.6mm is adopted as a filling material, and proper heat input is adjusted by changing the welding current, so that the defects of macroscopic welding cracks and the like in the welding process are improved, and welding seams with uniform and good forming are obtained.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211597562.XA CN115780967A (en) | 2022-12-13 | 2022-12-13 | Bottom layer welding process for ZGMn13Mo high manganese steel and A514 low alloy steel |
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| Application Number | Priority Date | Filing Date | Title |
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| CN202211597562.XA CN115780967A (en) | 2022-12-13 | 2022-12-13 | Bottom layer welding process for ZGMn13Mo high manganese steel and A514 low alloy steel |
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