CN115430888A - Welding method of nano precipitation strengthened steel - Google Patents
Welding method of nano precipitation strengthened steel Download PDFInfo
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- CN115430888A CN115430888A CN202110627244.2A CN202110627244A CN115430888A CN 115430888 A CN115430888 A CN 115430888A CN 202110627244 A CN202110627244 A CN 202110627244A CN 115430888 A CN115430888 A CN 115430888A
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- 238000000034 method Methods 0.000 title claims abstract description 44
- 238000001556 precipitation Methods 0.000 title abstract description 8
- 230000008569 process Effects 0.000 claims abstract description 15
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- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 20
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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
- B23K9/00—Arc welding or cutting
- B23K9/16—Arc welding or cutting making use of shielding gas
-
- 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
- B23K9/00—Arc welding or cutting
- B23K9/235—Preliminary treatment
-
- 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
- B23K9/00—Arc welding or cutting
- B23K9/24—Features related to electrodes
- B23K9/28—Supporting devices for electrodes
-
- 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
- B23K9/00—Arc welding or cutting
- B23K9/32—Accessories
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- Plasma & Fusion (AREA)
- Mechanical Engineering (AREA)
- Arc Welding In General (AREA)
Abstract
The invention discloses a welding method of nano precipitation strengthened steel, which is characterized in that proper pretreatment and preheating temperatures of the nano steel are adjusted by controlling welding process parameters and processes, the strength of an obtained welding seam is not reduced or increased, and a newly precipitated nano phase appears at the welding seam through synchrotron radiation and small-angle neutron scattering analysis at the welding seam.
Description
Technical Field
The invention relates to the technical field of welding, in particular to a welding method of nanometer precipitation strengthening steel.
Technical Field
With the development of science and technology, ultra-high strength steels are receiving more and more attention due to their great potential in terms of weight reduction and performance improvement, and thus the demand for advanced high strength steels is increasing in the fields of automobile manufacturing and mechanical engineering, etc. Taking an automobile as an example, at present, the automobile steel consumption plates in China account for about 61% of all steel consumption. The practical application strength of the girder plate of the truck and the passenger car in China is mostly 510-600 MPa, and the practical application strength of the girder plate of the truck and the passenger car reaches 700MPa, so that the strength of the girder plate of the truck and the passenger car is improved to 600-750 MPa in order to improve the load of the truck and not increase the self weight of the car body and improve the safety of the passenger car, and the light weight of steel becomes an important technical measure for realizing the purpose.
In recent years, with the development of nanotechnology, nanotechnology is applied to steel design, and the technology of precipitation strengthening of a nanoscale precipitated phase and prevention of grain growth is utilized, so that the strength and toughness, even the performances such as corrosion resistance, irradiation resistance and the like of structural steel are expected to be greatly improved, and a new way is developed for the design of novel high-strength special steel.
Welding is an important joining technique for the above-mentioned steel materials, and quality control of a welded joint plays an important role in practical application of the steel materials. The nanophase precipitation strengthening of the nano-strengthened ultrahigh-strength steel is the most important strengthening mode, and the structure of the nanophase precipitation is influenced by the bond of the strengthening effect, so that the effective control of the structure and the thermal stability of the nanophase precipitation is very important. However, when the argon tungsten-arc self-fusion welding method is used for connecting the nano materials, the nano phase (metastable phase) at the welding seam can be damaged, so that the strength of the welding seam is suddenly reduced, and finally, parts adopting the material are easy to lose effectiveness at the welding position in the using process. Therefore, the primary task of promoting the replacement of ordinary steel by the novel nano-reinforced steel is to prevent the sudden drop of the performance of the welded joint.
In order to solve the problem of influence of the welding process on the nano precipitated phase at the welding position, an improved welding method of the nano reinforced steel is needed.
Disclosure of Invention
In view of the above, the invention provides a welding method of a nanometer high-strength steel plate.
In order to achieve the above object, the present invention provides a method for welding a nano high-strength steel sheet, wherein the steel sheet to be welded is a nano precipitation-strengthened high-strength steel, and the tensile strength of the steel sheet is 1.1GPa, the method comprising the steps of:
step S1, pretreatment: namely, the steel plate to be welded is subjected to surface removal, polishing, oxidation removal and cleaning treatment;
s2, placing the two pretreated steel plates to be welded on a welding workbench to enable the two steel plates to be welded to be in close contact;
s3, preheating two steel plates to be welded for 2-10 min at 60-100 ℃ before formal welding;
and S4, welding by adopting self-fluxing welding, and continuously performing gas protection on the front side and the back side of the welding seam in the welding process until the temperature of the welding seam is reduced to room temperature, and then stopping protection.
As a further improvement of the invention, in the step S1, the surface of the steel plate is polished by sand paper or an electric grinder with 400 meshes to remove surface oxide skin, then the steel plate is ultrasonically cleaned by acetone solution for 5-10 min, finally the steel plate is ultrasonically cleaned by alcohol solution for 5-10 min, and then the steel plate is dried.
As a further improvement of the invention, in the step S1, the thickness h = 0.5-3 mm of the steel plate to be welded.
As a further improvement of the invention, in the step S2, two steel plates to be welded are closely contacted until the distance is less than one tenth of the thickness of the steel plates to be welded.
As a further improvement of the present invention, in step S4, argon is used as a shielding gas, and the self-fluxing welding parameters are as follows: the welding gun gas is 20L/min, the back shielding gas is 5-6L/min, the current I and the plate thickness h have the relation of I = n.h, n = 5-15 and the voltage is 60-80V according to the current parameters determined by the plate thickness.
As a further improvement of the present invention, in the step S4, at least 2 layers of stainless steel nets are disposed on the shielding gas nozzle to buffer the shielding gas.
Compared with the prior art, the invention has the beneficial effects that:
(1) Compared with the traditional nano steel welding process which reduces the strength and the hardness of a welding seam area, the method has the advantages that the welding process parameters and the welding process are controlled, the proper pretreatment and preheating temperature of the nano steel is adjusted, the strength of the obtained welding seam is not reduced or increased, a newly precipitated nano phase is obtained at the welding seam through the synchrotron radiation and small-angle neutron scattering analysis of the welding seam, and the problem that the strength of the welding seam area is suddenly reduced after the nano steel is welded can be well solved.
(2) The welding method of the nano reinforced steel plate does not use welding wires, is self-melting argon tungsten-arc welding, effectively reduces the production cost brought by the welding rods, and saves a large amount of cost for the subsequent large-scale nano high-strength steel welding application.
Drawings
To better illustrate the practical application of the invention, reference will now be made in brief to the accompanying drawings, which are used by way of example or in the prior art description.
Fig. 1 is a schematic diagram of a specific welding flow of the welding method of the nanometer high-strength steel of the present invention.
Fig. 2 is a mechanical test result of the welded nano high-strength steel used in the present invention, in which (a) a tensile curve of a nano steel weldment and a sample after tensile fracture are shown, and (b) hardness values of a substrate region and a weld region of the welded nano high-strength steel are shown.
Fig. 3 is a high-energy synchrotron radiation diagram of the nano high-strength steel after welding according to the present invention, which illustrates (a) a high-energy synchrotron radiation diagram of a substrate region and (b) a high-energy synchrotron radiation diagram of a weld region.
FIG. 4 is a diagram of a post-weld small-angle neutron scattering map of the post-weld nano high-strength steel of the present invention (a) a small-angle scattering fit in a weld region, and (b) a precipitated phase theoretical distance distribution function in the weld region.
Detailed Description
In order to make those skilled in the art better understand the technical solutions of the present invention, the technical solutions of the present invention will be clearly and completely described below with reference to the embodiments, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
The invention is further elucidated with reference to the figures and embodiments.
As shown in fig. 1, the present invention provides a welding method of a nanometer high-strength steel plate, wherein the steel plate to be welded is a nanometer precipitation-strengthened high-strength steel, and the tensile strength of the steel plate is 1.1GPa, the welding method comprises the following steps:
s1, a pretreatment link of two nano high-strength steel plates needing to be welded
The purification treatment mainly comprises the following steps: polishing and removing an iron oxide scale layer on the surface of 0-15 mm near a welding seam by using a sand paper/electric grinder, then placing two nano steel plates in an acetone solution for ultrasonic cleaning for 10min, placing in an absolute ethyl alcohol solution for ultrasonic cleaning for 10min after cleaning, and drying by using a blower for cold air drying so as to achieve the effect of removing oil stains and dirt.
And S2, placing the two processed nano high-strength steel plates on a welding workbench (a 2cm thick copper disc) and enabling the two steel plates to be in close contact, wherein the distance between the two steel plates is required to be less than one tenth of the thickness of the steel plates.
In order to bring the two steel plates into as close contact as possible, the steel plate contact portion needs to be ground as flat as possible (already completed at the purification treatment stage).
And S3, preheating the two steel plates to 60-100 ℃ for 2-10 min before formal welding, and measuring the temperature by a laser temperature measuring gun to ensure that the temperature of the steel plates can reach a preset value.
And S4, after preheating is finished, protecting the metal welding material by using shielding gas, melting the welding material on the welded substrate into a liquid state to form a molten pool by using a proper current (the relation between the current I and the plate thickness h is I = n.h, n = 5-15 and the voltage is 60-80V) according to current parameters determined according to the plate thickness, adopting a 12# gun for a straight-through gas welding gun, setting welding gun gas at 20L/min and back shielding gas at 5-6L/min, setting stainless steel nets on the welding gun and a back shielding gas nozzle, and setting the number of the net layers to be more than 2. The purpose of setting up the stainless steel net is on the one hand to play the buffering argon gas effect, can let gas more relax and the good guard action of density play, and on the other hand lets the argon gas take away more heats on the welder. The protective gas in the welding process is argon gas generally, or other inert gases can be selected, and the argon gas which does not react with the metal flows around the welding arc to form a protective gas cover so as to achieve the protective effect.
The nano precipitation-strengthened high-strength steel used in the following examples had a tensile strength of 1.1GPa and had the chemical composition, in weight percent, of Mn 1%, ni 1%, cu 2%, cr 3%, si 1.1%, mo 0.8%, al 0.5%, ti 0.3%, C0.11%, B0.02%, and the balance of Fe and inevitable impurities. Among them, the treatment process is referred to the following documents:
[1]Jiao Z B,Luan J H,Zhang Z W,et al.Synergistic effects of Cu and Ni on nanoscale precipitation and mechanical properties of high-strength steels[J].ACTA MATERIALIA,2013,61(16)：5996-6005.
[2]Jiao Z B,Luan J H,Miller M K,et al.Group precipitation and age hardening of nanostructured Fe-based alloys with ultra-high strengths[J].Scientific Reports,2016,6：21364.
[3]Zhou B C,Yang T,Zhou G,et al.Mechanisms for suppressing discontinuous precipitation and improving mechanical properties of NiAl-strengthened steels through nanoscale Cu partitioning[J].Acta Materialia,2020,205(4)：116561.。
example 1
The welding process is as shown in figure 1, firstly, an iron scale layer on the surface of a region, needing to be welded, of a nano high-strength steel plate with the tensile strength of 1.1GPa is polished by a sand paper/electric grinder to remove the oxide scale, and then ultrasonic cleaning is sequentially carried out through acetone and absolute ethyl alcohol solution; after airing, two nanometer high-strength steel plates are placed on a workbench (a 2cm thick copper disc has a heating function), the two steel plates are placed together as close to and stable as possible, and the size of each steel plate is 1.772mm in thickness (the actual thickness of a sample in hand at present, and the thickness of the sample during welding is unknown). Opening the heating function of the workbench, setting the temperature to be 70 ℃, keeping the temperature of the steel plate at about 70 ℃ after the workbench is heated to 70 ℃, measuring the temperature of the steel plate to be welded by using a laser temperature measuring gun after the temperature is kept for 5min, and starting formal welding after the preheating purpose is achieved; the welding current is related to the thickness of a weldment and is 20A, a 12# gun for a direct-ventilation (argon) welding gun is adopted, the gas of the welding gun is 20L/min, the back shielding gas is 5L/min, both the welding gun and the back shielding gas need to be provided with meshes, and the number of the meshes is more than 2. And heating the welding seam area by using high current, and stopping heating after the self-melting of the area to be welded is completely liquid, thereby completing the whole welding process.
In order to better detect the superiority of the welding method, a welded sample is cut into a dog bone model as shown in the figure, a tensile test is carried out, a tensile test mechanical curve and a tensile fracture sample are shown in figure 2 (a), and it can be seen from the figure that the fracture of the welded tensile piece occurs outside a weld seam area, the welded tensile piece has an obvious necking phenomenon and the tensile fracture position is not in the weld seam area. In addition, the sample after welding was subjected to a hardness test, as shown in fig. 2 (b) (vickers Hardness (HV) value in ordinate), and found that the hardness in the weld zone was larger than that in the base zone.
In order to explore the difference of the strength and the hardness of a welded area and a non-welded area of the welded nano steel, a welded sample is subjected to synchrotron radiation testing on the welded area and a substrate area respectively, and the result is fitted according to synchrotron radiation data: FIG. 3 (a) shows that the nano-steel matrix region has alpha-Fe composition, and FIG. 3 (b) shows that the nano-steel weld region has fine Ni in addition to alpha-Fe 3 Al phase composition and may have a corresponding Ni around 2 theta =3.8 DEG 3 The peak of Al is obtained by comparing the two graphs in FIG. 4, and the nano steel generates a new phase in the welding seam area after welding.
In order to better explore the new phase generated in the welded seam region, the welded seam region of the welded part is subjected to a small-angle scattering test, and the obtained results are shown in fig. 4, wherein fig. 4 (a) is an I (Q) fitting curve, and fig. 4 (b) is small-angle neutron scatteringP (r) in the graph is a distance distribution function, which means that the structural information of the sample real space is reflected among crystal grains, and (b) the graph shows that the precipitated phase is a spherical structure and the distance among the obtained crystal grains is mainly 30-40nm, and Ni is judged 3 The Al phase is a nano precipitated phase.
In conclusion, when the welding method of the invention is used for welding the nanometer high-strength steel, new nanometer precipitated phases are generated in the welding seam area, and the precipitated phases enable the welding seam area to have higher strength and higher hardness, so that the tensile fracture position of a welded sample is generated in a non-welding seam area.
Compared with the prior art, the welding method of the nanometer high-strength steel plate enables the welding line area to form a new nanometer phase through proper pretreatment and preheating temperature of the nanometer steel and optimization of welding process parameters and welding process, and enables the strength and the hardness of the welding line area to be stronger than those of the matrix area.
The welding method of the nano reinforced steel plate provided by the invention not only can not reduce the strength and hardness of the welding seam area but also can improve the strength and hardness of the welding seam area, and is obviously stronger than that of the traditional welding method at present. In addition, the welding method of the nano reinforced steel plate does not use welding wires, is self-fluxing argon tungsten-arc welding, effectively reduces the production cost brought by the welding wires, and saves a large amount of cost for the large-scale nano high-strength steel welding application. It is worth mentioning that through proper preheating treatment, proper gas injection speed and reasonable current and voltage, the strength of the welding position of the nanometer reinforced steel plate is higher than that of the base metal, and the toughness of the welding position of the nanometer reinforced steel plate is equal to that of the base metal, so that the problem that the strength and the toughness of the welding joint of the 1.1 GPa-grade nanometer high-strength steel plate are suddenly reduced after the welding by using the traditional welding method is obviously solved.
Claims (6)
1. A welding method of a nanometer high-strength steel plate is characterized in that the steel plate to be welded is nanometer precipitation-strengthened high-strength steel, the tensile strength of the steel plate is 1.1GPa, and the welding method comprises the following steps:
step S1, preprocessing: namely, the surface of the steel plate to be welded is polished, oxidized and cleaned;
s2, placing the two pretreated steel plates to be welded on a welding workbench to enable the two steel plates to be welded to be in close contact;
s3, preheating two steel plates to be welded at 60-100 ℃ for 2-10min before formal welding;
and S4, welding by adopting self-fluxing welding, and continuously performing gas protection on the front side and the back side of the welding seam in the welding process until the temperature of the welding seam is reduced to room temperature, and then stopping protection.
2. The method of claim 1, wherein in step S1, the surface of the steel plate is polished by a 400-mesh sand paper or an electric grinder to remove surface oxide skin, and then is ultrasonically cleaned by an acetone solution for 5-10 min, finally is ultrasonically cleaned by an alcohol solution for 5-10 min, and is dried.
3. A method according to claim 1, characterised in that in step S1 the thickness h =0.5 to 3mm of the steel sheet to be welded.
4. A method according to claim 1, wherein in step S2, the two steel plates to be welded are brought into close contact until the distance is less than one tenth of the thickness of the steel plates to be welded.
5. The method of claim 1, wherein in step S4, argon is used as a shielding gas, and the autogenous welding parameters are as follows: the welding gun gas is 20L/min, the back shielding gas is 5-6L/min, the relation between the current I and the plate thickness h is I = n.h, n = 5-15, and the voltage is 60-80V according to current parameters determined by the plate thickness.
6. The method of claim 1, wherein in step S4, the shielding gas is buffered by disposing at least 2 layers of stainless steel mesh on the shielding gas nozzle.
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| CN103753023A (en) * | 2014-02-14 | 2014-04-30 | 苏州大学 | Welding method of hot-rolled nano reinforced steel plates |
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| CN103753023A (en) * | 2014-02-14 | 2014-04-30 | 苏州大学 | Welding method of hot-rolled nano reinforced steel plates |
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| Title |
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| 张毅斌;: "一种铜沉淀强化铁素体钢焊接热影响区性能研究", 材料开发与应用, no. 05, pages 6 - 30 * |
| 赵宇: "富铜纳米相沉淀强化钢强韧化机制及可焊性研究", 《中国博士学位论文全文数据库 (工程科技Ⅰ辑)》, no. 04 * |
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