CN109746549A - A kind of high-strength light welded steel technique - Google Patents
A kind of high-strength light welded steel technique Download PDFInfo
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- CN109746549A CN109746549A CN201910213537.9A CN201910213537A CN109746549A CN 109746549 A CN109746549 A CN 109746549A CN 201910213537 A CN201910213537 A CN 201910213537A CN 109746549 A CN109746549 A CN 109746549A
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Abstract
The invention belongs to welding technology fields, disclose a kind of high-strength light welded steel technique, comprising the following steps: steel to be welded are kept the temperature 20~30min by preheating at a temperature of 300~350 DEG C, the steel with a thickness of 2~3.5mm；Welding is welded to obtain weldment using TIG weld technique, and weldingvoltage is 10~14V, and welding current is 120~160A, uses inert gas as protective gas in welding process, protective gas flow velocity is 7~9L/min, 13~17cm/min of speed of welding；The weldment for using step 2 to obtain is put into temperature in 1000~1100 DEG C of heat-treatment furnaces, to keep the temperature 30~45min by solution treatment, and rear take out is put into cooling in 20~35 DEG C of cooling medium.The technical solution in the present invention is used to provide a kind of welding procedure for Fe-Mn-Al-C system low density steel, obtained workpiece high mechanical properties.
Description
Technical field
The invention belongs to welding technology fields, and in particular to a kind of high-strength light welded steel technique.
Background technique
With China's economic sustained and rapid development, vehicle guaranteeding organic quantity continued to keep rapid growth situation, by 2018
Bottom, national vehicle guaranteeding organic quantity is up to 3.27 hundred million.Research shows that: vehicle fuel consumption and the self weight of its vehicle body are linear,
Under the premise of other conditions are constant, vehicle weight is every to reduce 10%, and fuel consumption can reduce by 6~8%, and every fuel oil for reducing 1L
Consumption will discharge the CO of 2.45kg less2, it is seen that it is very big for reducing influence of the discharge of vehicle exhaust to environment.In addition,
In aerospace field, the loss of weight of spacecraft is also to mean a great, and not only reduces oil consumption, reduces discharge, also reduce operation at
This, and then promote voyage.
Fe-Mn-Al-C system low density steel, since it has the advantages that excellent mechanical property and low-density, corrosion-resistant,
It can be developed as low energy consumption, low CO2The advantages of lightweight body of a motor car material of discharge, this low-density and high-strength, depends on one
The addition of a little light elements, such as C, Al, Mn, the addition of these elements also determine the phase structure of material.Stablize member according to austenite
The ratio of element (Mn, C) and ferrite former (Al, Si), it is double that ferrimanganic aluminium carbon steel can be divided into austenite one phase steel, austenite base
Xiang Gang, ferrite base dual phase steel and the single-phase steel of ferrite are being sought without the mechanical property difference of ferrimanganic aluminium carbon steel of the same race
One kind both having had high-intensitive and high-corrosion resistance, while but also with the ferrimanganic aluminium carbon steel compared with low-density, inventor has been done largely
Test.
Additionally, due to current Fe-Mn-Al-C system low density steel also in theoretical research stage, actual life is not put into also
Produce in application, thus the series material preparation and welding procedure be in stage of exploration, and the common side of welding of steel
Formula, such as arc welding, CO2Protection weldering etc. finds these techniques to Fe-Mn-Al-C system low density steel by the test of inventor
There are many detrimental effects in welding performance, therefore the present invention predominantly finds one kind and is suitable for Fe-Mn-Al-C system low density steel
Welding procedure, guarantee Fe-Mn-Al-C system low density steel welding after mechanical property promoted.
Summary of the invention
The invention is intended to provide a kind of welding procedure suitable for high-strength low-density steel, after being welded with lifting workpieces
Mechanical property.
To achieve the above object, the present invention provides following base case: a kind of high-strength light welded steel technique, the steel
The chemical general formula of material is Fe-28Mn-10Al-0.8C, comprising the following steps:
Step 1: steel to be welded are kept the temperature 20~30min, the thickness of the steel by preheating at a temperature of 300~350 DEG C
Degree is 2~3.5mm；
Step 2: welding is welded to obtain weldment using TIG weld technique, and weldingvoltage is 10~14V, welding electricity
Stream is 120~160A, uses inert gas as protective gas in welding process, and protective gas flow velocity is 7~9L/min, welding
13~17cm/min of speed；
Step 3: the weldment for using step 2 to obtain is put into temperature as 1000~1100 DEG C of heat-treatment furnaces by solution treatment
In, 30~45min is kept the temperature, rear take out is put into cooling in 20~35 DEG C of cooling medium, obtains solid solution part, and the solid solution part is Austria
Fe is distributed in the austenite one phase structure in family name's body phase structure3C phase.
The technical program the utility model has the advantages that
Inventor has developed a kind of high-strength light welded steel technique, inventor is in R&D process by largely studying
In use the most common two kinds of welding procedures of welded steel first, first is that arc welding, to the welded steel in the present invention it
After find, a large amount of Al2O3Occur, so that weld seam forms a large amount of crackle, the mechanical property of weldment is significantly reduced；
Second is that CO2Protection weldering, finds, the Al formed in weld seam after welding to the steel in the present invention2O3It reduces, but obtain
Weldment coarse grains, a sharp decline such as mechanical property such as tensile strength, moulding.
And inventor largely researchs and analyses to have obtained the welding in this programme by having carried out to the steel in the present invention
Technique.
In conclusion the technical program has following technical effect that
1, after warming, the organization softening in welded steel region, effect is steel in this programme, on the one hand, softening
When group afterwards is woven in welding, the welding slag to splash outward is reduced, and the risk to operator is reduced, on the other hand, compared to not
The mode directly welded is preheated, since the high temperature electrode in this kind of mode TIG weld is contacted with the steel of low temperature (room temperature),
The crystal grain in welded steel area is promoted to grow up, so that the brittleness of weld seam improves, moulding is reduced, and the height in this programme in TIG weld
Warm electrode is contacted with the steel of high temperature (300~350 DEG C), smaller on the influence of the crystal grain of welding section, and crystal grain will not quickly be grown.
2, the weldment as obtained in step 2 is ferrite and austenite two phase structure in this programme, in order to further
The tensile property of weldment is improved, therefore carries out carrying out solution treatment to weldment, the purpose of inventor is solution treatment process
It is middle that ferrite is dissolved in austenite, austenite one phase tissue is formed, and then improve the mechanical property of solid solution part, and inventor
It is found by this programme, ferrite also creates a large amount of Fe during being dissolved into austenite3C phase.
And generate Fe3The reason of C phase, is in the high-strength light steel researched and developed due to us that Al, Mn atom content are higher,
When solution treatment, a large amount of Al, Mn atom is dissolved into austenite, so that austenite is in oversaturated state, simultaneously because iron
Ferritic forms vacancy, in cooling procedure, oversaturated state makes part in austenite during being dissolved in austenite
Fe and C element enter in vacancy, form Fe3C compound, and since the cooling velocity of weldment in this programme is exceedingly fast, Fe3Cization
Close object to have little time to grow up, therefore be present in austenite phase in the form of micron-sized, and by inventor's it is demonstrated experimentally that using
The solid solution part tensile strength that this programme obtains is higher.
Further, the steel in the step 1 before preheating, derust to the surface of steel, degreasing and burnishing part
Reason.
The utility model has the advantages that processing is the influence for avoiding the rusty stain or greasy dirt of steel surface to weld seam is formed in this way.
Further, the inert gas in the step 2 is the argon gas that purity is higher than 99.99%.
The utility model has the advantages that the chance that the Al atom when argon gas of high-purity is to reduce welding in steel is contacted with oxygen,
Reduce Al in weld seam2O3Content, and then improve weldment mechanical property.
Further, the weldment in the step 3 at once beats weld seam after weld seam solidifies.
The utility model has the advantages that since the deformation of welding stress and weld seam is mainly that postwelding weld seam occurs caused by shortening,
So that weld seam is suitably extended elongation, shortening can be compensated, to reduce welding stress and distortion；Therefore after the completion of welding, pass through
Tapping to weld seam can extension weld seam appropriate, reduction stress and deformation.
Further, the cooling medium in the step 3 is oil or water.
The utility model has the advantages that cooling medium enough guarantees that being dissolved part keeps austenite one phase structure, is dissolved into Austria using oil or water energy
The elements such as Mn, Al of family name's body have little time to be precipitated, and cause austenite distortion of lattice, inhibit dislocation motion, while Fe3C phase has little time
It grows up, is distributed in austenite structure with micron scale construction, play the role of dispersion-strengtherning.
Further, the Fe-28Mn-10Al-0.8C steel raw material include mass percent be 60.36% pure iron,
0.09% vanadium iron, 0.11% ferro-niobium, 0.85% graphitic carbon, 28% electrolytic manganese, 10.5% aluminium block and 0.09%
Pure titanium.
The utility model has the advantages that reaching 875MPa, density using Fe-28Mn-10Al-0.8C steel strength prepared by said ratio
For 6.65g/cm3, compared with pure iron density 7.86g/cm3, density reduces 15.4%, has excellent loss of weight potentiality.
Further, the preparation process of the Fe-28Mn-10Al-0.8C steel, comprising the following steps:
Step (1): charging, by mass percent be 60.36% pure iron, 0.09% vanadium iron, 0.11% ferro-niobium and
0.05% graphitic carbon is placed in the crucible of vaccum sensitive stove, by 28% electrolytic manganese, 0.8% graphitic carbon, 10.5%
Aluminium block and 0.09% pure titanium are individually positioned in the raw material tank of vaccum sensitive stove, and vacuumizing drops to pressure in vaccum sensitive stove
20Pa or less；
Step (2): fusing, starting vaccum sensitive stove makes the melting sources in crucible, after raw material is completely melt, closes electricity
Source；
Step (3): alloying is again turned on the power supply of vaccum sensitive stove, is heated using 30~35KW power, by raw material tank
In electrolytic manganese and graphitic carbon be added in crucible, aluminium block in raw material tank and pure titanium are added in crucible after 10~15min；0.8
Vacuum is removed after~1.5h, steel tapping casting obtains steel ingot after cooling；
Step (4): forging, the steel ingot that step 3 is obtained carries out just forging at a temperature of 1050~1100 DEG C, in 850~900
Finish-forging is carried out at a temperature of DEG C, is air-cooled to room temperature after finish-forging.
The technical program the utility model has the advantages that
Less using field trash in the steel of above-mentioned technique preparation, the purity of steel is higher, mechanical property and processing performance
Preferably.
Further, the raw material in the step of preparation process (1) of the Fe-28Mn-10Al-0.8C steel is right before charging
The surface of raw material carries out derusting and degreasing processing.
The utility model has the advantages that the content of inclusion content in melting steel can be reduced as far as possible by carrying out derusting and degreasing processing, steel ingot is improved
Purity.
Further, in the step of preparation process (2) of the Fe-28Mn-10Al-0.8C steel include three phases, first
Stage, vaccum sensitive stove heating power are 10KW, heating time 10min；The power of vaccum sensitive stove is adjusted to by second stage
50KW, until raw material are completely melt as molten steel；Phase III, by the power decreasing of vaccum sensitive stove to 30KW, 30~35min
The power supply of vaccum sensitive stove is closed afterwards.
The utility model has the advantages that heating stage by stage is so that raw material successively melts, and the mode successively melted makes the gas in raw material
Body and non-metallic inclusion are also layer-by-layer to be discharged, and avoids the fusing that raw material is too fast, internal gas and Slag inclusion come not
And discharge is dissolved in molten steel.
Further, the steel ingot in the step of preparation process (4) of the Fe-28Mn-10Al-0.8C steel is put before forging
Enter in heat-treatment furnace, be heated to 1180 DEG C, keeps the temperature 2h.
The utility model has the advantages that the purpose handled in this way is the homogenization of composition so that in steel ingot, so that the alloy in steel ingot is equal
Even is diffused into each crystal grain, reduces alloy in the aggregation of grain boundaries, and then improve the plasticity of steel ingot.
Detailed description of the invention
Fig. 1 is a kind of process schematic representation of high-strength light welded steel process example 1 of the present invention；
Fig. 2 is a kind of weld seam metallographic structure figure that high-strength light welded steel process example 1 obtains of the present invention；
Fig. 3 is a kind of tensile stress strain curve figure of 1 commissure of high-strength light welded steel process example of the present invention；
Fig. 4 is a kind of weld seam metallographic structure figure that high-strength light welded steel process example 6 obtains of the present invention；
Fig. 5 is a kind of tensile stress strain curve figure of 6 commissure of high-strength light welded steel process example of the present invention.
Specific embodiment
It is further described below by specific embodiment:
The present invention provides a kind of high-strength light welded steel technique, wherein used in the present invention chemical general formula of steel for
Fe-28Mn-10Al-0.8C, raw material include mass percent be 60.36% pure iron, 0.09% vanadium iron, 0.11% niobium
Iron, 0.85% graphitic carbon, 28% electrolytic manganese, 10.5% aluminium block and 0.09% pure titanium, the preparation process packet of the steel
Include following steps:
Step (1): charging carries out derusting to the surface of above-mentioned raw materials before charging and degreasing is handled, after by quality hundred
Divide than being that 60.36% pure iron, 0.09% vanadium iron, 0.11% ferro-niobium and 0.05% graphitic carbon are placed on vaccum sensitive stove
Crucible in, 28% electrolytic manganese, 0.8% graphitic carbon, 10.5% aluminium block and 0.09% pure titanium are individually positioned in very
In the raw material tank of empty induction furnace, opening vacuum pump set and vacuumizing makes pressure in vaccum sensitive stove drop to 20Pa or less.
Step (2): fusing, starting vaccum sensitive stove make the melting sources in crucible, including three phases, the first stage,
Vaccum sensitive stove heating power is 10KW, heating time 10min；The power of vaccum sensitive stove is adjusted to 50KW by second stage,
Until the raw material in crucible are completely melt as molten steel；Phase III, by the power decreasing of vaccum sensitive stove to 30KW, 30~
The power supply that vaccum sensitive stove is closed after 35min, since oxygen most of in raw material at this time is reacted with graphitic carbon, generation CO or CO2, separately
Volatile impurity discharge in outer raw material, so that the vacuum degree of vaccum sensitive stove reduces, it is therefore desirable to again to vaccum sensitive stove
Vacuumize process, specifically: charging valve is opened, argon gas is filled with into vaccum sensitive stove, opens simultaneously vacuum pump set, until true
Pressure in empty induction furnace is down to 0.12MPa or less.
Step (3): alloying is again turned on the power supply of vaccum sensitive stove, is heated using 30~35KW power, by raw material tank
In electrolytic manganese and graphitic carbon be added in crucible, aluminium block in raw material tank and pure titanium are added in crucible after 10~15min；0.8
~1.5h or so removes vacuum, that is, opens the vent valve of vaccum sensitive stove, make in vaccum sensitive stove after the liquid level of molten steel is steady
Air pressure restore atmospheric pressure, steel tapping casting obtains steel ingot after cooling, after steel ingot be put into heat-treatment furnace be heated to 1180 DEG C,
2h is kept the temperature, Homogenization Treatments are carried out.
Step (4): forging, the steel ingot that step 3 is obtained carries out just forging at a temperature of 1050~1100 DEG C, in 850~900
Finish-forging is carried out at a temperature of DEG C, is air-cooled to room temperature after finish-forging.
The Fe-28Mn-10Al-0.8C steel tensile strength prepared by above-mentioned technique reaches 875MPa, with pure iron tension
170~270MPa of intensity is compared, and the tensile strength of the steel increases substantially, and in addition Fe-28Mn-10Al-0.8C steel is close
Degree is 6.65g/cm3, with pure iron density 7.86g/cm3It compares, density reduces 15.4%, has excellent loss of weight potentiality.
A kind of high-strength light welded steel technique of the present invention, inventor have been obtained through a large number of experiments in ginseng of the invention
In number ranges, the tensile strength of obtained workpiece is high, the stability of tissue is preferable, and listed in the application 10 groups therein into
Explanation is gone.
Each technological parameter in a kind of embodiment 1-10 of the high-strength light welded steel technique of table 1
Now by taking embodiment 1 as an example, a kind of high-strength light welded steel technique of the present invention is illustrated.
A kind of high-strength light welded steel technique, includes the following steps, as shown in Figure 1, being showing for the technique of the present embodiment
It is intended to:
Step 1: preheating first carries out grinding process using periphery of the abrasive machine to steel before preheating, until steel is outer
Zhou Guangliang, then the processing that degreases is carried out to Fe-28Mn-10Al-0.8C steel surface using acetone, by treated, steel exist
20min is kept the temperature in heat-treatment furnace at a temperature of 300 DEG C.
Step 2: welding, using TIG weld technique, i.e. non-melt pole Heliarc welding, weldingvoltage is
10V, the electric current of welding are 120A, use argon gas of the purity higher than 99.99% as protective gas, protective gas in welding process
Flow velocity be 7L/min, speed of welding 13cm/min；Weldment is obtained after the completion of welding, the weld seam solidification of to-be-welded pieces finishes
Afterwards, at once using the weld seam of tool hammer tapping weldment, tool hammer taps the vibration generated so that the stress of weld seam is released.
Step 3: the weldment being cooled to room temperature in step 2 being fitted into the heat-treatment furnace that temperature is 1000 DEG C, heat preservation
30min, rear take out are put into temperature to be cooled down in 20 DEG C of water, and cooling time is not less than 5min, solid solution part is obtained, wherein solid
Molten part is austenite one phase structure, and Fe is distributed in austenite one phase structure3C phase.
Embodiment 2-10 is identical as the welding procedure of embodiment 1, and difference is only that each technological parameter as shown in Table 1 not
Together.
In addition 6 groups of comparative examples are set and embodiment 1-10 compares experiment.
Table 2 is each technological parameter of comparative example 1-6 (" -- " indicates without the parameter)
Comparative example 1-5 is identical as the steel that embodiment 1-10 is used, and difference is only that welding parameter as shown in Table 2 not
Together, comparative example 6 is not the difference from embodiment 1 is that pass through solutionizing step.
Following experiment is carried out using the workpiece that embodiment 1-10, comparative example 1-6 are provided:
1, tensile tests at room:
By the work pieces process for using the technique of embodiment 1-10 and comparative example 1-6 to prepare for tensile test specimen, the day island proper is utilized
The model AGS-X 100KN tensile testing machine of saliva production, maximum test load 100KN, test load precision are show value
Within ± 0.5%, test rate adjusting range is 0.001~800mm/min, and velocity accuracy is ± 0.1%, and return speed is
1100mm/min, position detection resolution ratio are 0.033 μm, data sampling interval: 1ms.
The tensile test specimen of embodiment 1-10, comparative example 1-6 are put into tensile testing machine, and clamped, so that sample is in nothing and answers
Power state.It in test software alignment load and is zeroed, inputs tensile sample size, set rate of extension as 3mm/min.Start
Rate tensile is determined, until sample fracture, saves data.As shown in table 3, a indicates the tensile strength (MPa) of each test specimen in table 3；b
Indicate the strain (%) that each test specimen is broken.
It as shown in Figure 2 and Figure 4, is the tensile stress strain curve figure of embodiment 3 and embodiment 6, it can from Fig. 2 and Fig. 4
To find out, the elastic deformation stage of tensile sample is shorter, is 300MPa or so in stress, strains when being 1.5% or so, stretches examination
Stress suffered by sample increases rapidly.When strain is 1.5% to 8% stage, tensile sample has begun generation plastic deformation, but
Rate of stressing is much larger than conventional strain.When strain is greater than 8%, into strain, at this time test specimen is strong
Degree increases with strain, and improving speed becomes more slowly, after the tensile strength that reaches capacity, to be broken quickly, constriction rank
Section is very short.It is possible thereby to show that the tensile strength of test specimen is larger, and the strain that the plastic deformation stage bears is larger.
Strain table when table 3 is the tensile strength and fracture of each test specimen of embodiment 1-10
| Embodiment | 1 | 2 | 3 | 4 | 5 | 6 | 7 | 8 | 9 | 10 |
| a | 880 | 875 | 860 | 850 | 865 | 825 | 840 | 855 | 820 | 815 |
| b | 36 | 36 | 36.2 | 36.8 | 36.2 | 37.5 | 37 | 36.6 | 37.8 | 38 |
Strain table when table 4 is the tensile strength and fracture of each test specimen of comparative example 1-6
| Comparative example | 1 | 2 | 3 | 4 | 5 | 6 |
| a | 755 | 740 | 690 | 745 | 705 | 460 |
| b | 23 | 22.4 | 20.2 | 23 | 21 | 12 |
By table 3 and table 4 it is found that using welding procedure provided in the present invention, obtained workpiece tensile strength is high, and moulding becomes
The strain born during shape is larger, wherein with the technological parameter of embodiment 1 be it is best, tensile strength has been even more than base material
Tensile strength, the mechanical property of weld seam is greatly improved, and low without the workpiece tensile strength of solutionizing step,
The strain that can be born during plastic deformation is also smaller.
2, metallographic detects:
It uses wire cutting to cut the bulk of 10 × 5 × 2mm the weldment that embodiment 1-10, comparative example 1-6 are provided, utilizes
Model ECLIPSE MA200, Nikon optical microscopy produced carry out metallographic observation.Using Nikon CFI60 optical system,
Amplification factor is 50~2000 times, then the illumination of 12V100W halogen lamp carries out cold edge sample method to prepare diameter being 30mm with resin
Inlaying samples.
Next it is successively ground using the artificial hand of the abrasive paper for metallograph of 200#, 400#, 600#, 800#, 1000#, 1200# model,
Then sample surfaces are processed by shot blasting on polishing machine using diamond polishing cream, make specimen surface smooth mirror surface.It throws
Sample after light is corroded using 6% nital, and the time of corrosion is substantially after 1.5min or so, corrosion with a large amount of
Distilled water flushing, then alcohol rinse, uses hair dryer hot blast drying at the same time.Finally using optical microscopy to treated
Sample carries out metallographic structure observation.
By taking embodiment 1 and embodiment 6 as an example, as shown in Fig. 3 and Fig. 5, solid solution part is the homogeneous structure structure of austenite, and
Dispersed precipitate has a large amount of micron-sized Fe in austenite3C phase, and the Fe being precipitated in Fig. 53Al phase compared to more in Fig. 3,
But in conjunction with stretching experiment it is found that the tensile strength of the resulting solid solution part of embodiment 6 will be lower than embodiment 1, therefore in solution treatment
The Fe formed in the process3C phase is not The more the better.
What has been described above is only an embodiment of the present invention, and the common sense such as well known specific structure and characteristic are not made herein in scheme
Excessive description.It, without departing from the structure of the invention, can be with it should be pointed out that for those skilled in the art
Several modifications and improvements are made, these also should be considered as protection scope of the present invention, these all will not influence what the present invention was implemented
Effect and patent practicability.The scope of protection required by this application should be based on the content of the claims, in specification
The records such as specific embodiment can be used for explaining the content of claim.
Claims (10)
1. a kind of high-strength light welded steel technique, it is characterised in that: the chemical general formula of the steel is Fe-28Mn-10Al-
0.8C, comprising the following steps:
Step 1: steel to be welded are kept the temperature 20~30min by preheating at a temperature of 300~350 DEG C, the steel with a thickness of
2~3.5mm；
Step 2: welding is welded to obtain weldment using TIG weld technique, and weldingvoltage is 10~14V, and welding current is
120~160A, is used as protective gas using inert gas in welding process, and protective gas flow velocity is 7~9L/min, speed of welding
13~17cm/min；
Step 3: the weldment for using step 2 to obtain is put into temperature to protect in 1000~1100 DEG C of heat-treatment furnaces by solution treatment
30~45min of temperature, rear take out are put into cooling in 20~35 DEG C of cooling medium, obtain solid solution part, and the solid solution part is austenite
Fe is distributed in the austenite one phase structure in phase structure3C phase.
2. a kind of high-strength light welded steel technique according to claim 1, it is characterised in that: the steel in the step 1
Material before preheating, derusts to the surface of steel, degreasing and grinding process.
3. a kind of high-strength light welded steel technique according to claim 1, it is characterised in that: lazy in the step 2
Property gas be purity be higher than 99.99% argon gas.
4. a kind of high-strength light welded steel technique according to claim 1, it is characterised in that: the weldering in the step 2
Fitting at once beats weld seam after weld seam solidifies.
5. a kind of high-strength light welded steel technique according to claim 1, it is characterised in that: cold in the step 3
But medium is oil or water.
6. a kind of high-strength light welded steel technique described in any one according to claim 1~5, it is characterised in that: described
Fe-28Mn-10Al-0.8C steel raw material includes that mass percent is 60.36% pure iron, 0.09% vanadium iron, 0.11%
Ferro-niobium, 0.85% graphitic carbon, 28% electrolytic manganese, 10.5% aluminium block and 0.09% pure titanium.
7. a kind of high-strength light welded steel technique according to claim 6, it is characterised in that: the Fe-28Mn-
10Al-0.8C the preparation process of steel the following steps are included:
Step (1): charging, by mass percent be 60.36% pure iron, 0.09% vanadium iron, 0.11% ferro-niobium and
0.05% graphitic carbon is placed in the crucible of vaccum sensitive stove, by 28% electrolytic manganese, 0.8% graphitic carbon, 10.5%
Aluminium block and 0.09% pure titanium are individually positioned in the raw material tank of vaccum sensitive stove, and vacuumizing drops to pressure in vaccum sensitive stove
20Pa or less；
Step (2): fusing, starting vaccum sensitive stove makes the melting sources in crucible, after raw material is completely melt, closes power supply；
Step (3): alloying is again turned on the power supply of vaccum sensitive stove, is heated using 30~35KW power, will be in raw material tank
Electrolytic manganese and graphitic carbon are added in crucible, will be in the aluminium block and pure titanium addition crucible in raw material tank after 10~15min；0.8~
Vacuum is removed after 1.5h, steel tapping casting obtains steel ingot after cooling；
Step (4): forging, the steel ingot that step 3 is obtained carries out just forging at a temperature of 1050~1100 DEG C, in 850~900 DEG C of temperature
Degree is lower to carry out finish-forging, is air-cooled to room temperature after finish-forging.
8. a kind of high-strength light welded steel technique according to claim 7, it is characterised in that: the Fe-28Mn-
Raw material in the step of preparation process (1) of 10Al-0.8C steel carries out derusting and degreasing to the surface of raw material before charging
Processing.
9. a kind of high-strength light welded steel technique according to claim 7, it is characterised in that: the Fe-28Mn-
It include three phases in the step of preparation process (2) of 10Al-0.8C steel, the first stage, vaccum sensitive stove heating power is
10KW, heating time 10min；The power of vaccum sensitive stove is adjusted to 50KW by second stage, until raw material be completely melt for
Molten steel；The power decreasing of vaccum sensitive stove to 30KW is closed the power supply of vaccum sensitive stove by the phase III after 30~35min.
10. a kind of high-strength light welded steel technique according to claim 7, it is characterised in that: the Fe-28Mn-
Steel ingot in the step of preparation process (4) of 10Al-0.8C steel is put into heat-treatment furnace before forging, is heated to 1180 DEG C,
Keep the temperature 2h.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114769938A (en) * | 2022-04-24 | 2022-07-22 | 燕山大学 | Metal flux-cored wire and preparation method and application thereof |
Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103894708A (en) * | 2014-03-18 | 2014-07-02 | 上海振华重工(集团)股份有限公司 | All-position narrow gap hot filament inert gas tungsten electrode shielded welding process |
| CN104942410A (en) * | 2015-07-16 | 2015-09-30 | 上海振华重工(集团)股份有限公司 | Ultra-narrow gap TIG (tungsten inert gas) hot wire welding method |
| EP2952608A1 (en) * | 2014-06-02 | 2015-12-09 | Apogean Metal Incorporation | Fe-Mn-Al-C alloy and method for manufacturing the same |
| CN105750846A (en) * | 2016-05-12 | 2016-07-13 | 中国兵器工业第五九研究所 | Quick forming method of low-alloy high-strength steel deep hole component |
| CN106521318A (en) * | 2016-11-22 | 2017-03-22 | 河北工业大学 | High-strength Fe-Mn-Al-C-series low density cast steel and preparation method thereof |
| CN106670626A (en) * | 2016-11-11 | 2017-05-17 | 山东省科学院海洋仪器仪表研究所 | Dual-magnetic-control arc narrow-gap double-sided welding process |
| CN106808058A (en) * | 2017-01-22 | 2017-06-09 | 大连理工大学 | A kind of repair method of austenitic stainless steel casting core pump case |
| CN107058854A (en) * | 2017-03-13 | 2017-08-18 | 昆明理工大学 | A kind of vacuum smelting method of the high manganese high-aluminum steel of Nb, V, Ti microalloying |
| CN107675098A (en) * | 2016-12-05 | 2018-02-09 | 东北大学 | A kind of preparation method of lightweight high manganese steel material |
| CN108486506A (en) * | 2018-05-31 | 2018-09-04 | 中北大学 | A kind of preparation method and application of high-performance low-density steel plate |
| CN108642403A (en) * | 2018-05-28 | 2018-10-12 | 河北工业大学 | A kind of 780MPa grade super strengths Fe-Mn-Al-C systems lightweight cast steel and preparation method thereof |
-
2019
- 2019-03-20 CN CN201910213537.9A patent/CN109746549A/en active Pending
Patent Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103894708A (en) * | 2014-03-18 | 2014-07-02 | 上海振华重工(集团)股份有限公司 | All-position narrow gap hot filament inert gas tungsten electrode shielded welding process |
| EP2952608A1 (en) * | 2014-06-02 | 2015-12-09 | Apogean Metal Incorporation | Fe-Mn-Al-C alloy and method for manufacturing the same |
| CN104942410A (en) * | 2015-07-16 | 2015-09-30 | 上海振华重工(集团)股份有限公司 | Ultra-narrow gap TIG (tungsten inert gas) hot wire welding method |
| CN105750846A (en) * | 2016-05-12 | 2016-07-13 | 中国兵器工业第五九研究所 | Quick forming method of low-alloy high-strength steel deep hole component |
| CN106670626A (en) * | 2016-11-11 | 2017-05-17 | 山东省科学院海洋仪器仪表研究所 | Dual-magnetic-control arc narrow-gap double-sided welding process |
| CN106521318A (en) * | 2016-11-22 | 2017-03-22 | 河北工业大学 | High-strength Fe-Mn-Al-C-series low density cast steel and preparation method thereof |
| CN107675098A (en) * | 2016-12-05 | 2018-02-09 | 东北大学 | A kind of preparation method of lightweight high manganese steel material |
| CN106808058A (en) * | 2017-01-22 | 2017-06-09 | 大连理工大学 | A kind of repair method of austenitic stainless steel casting core pump case |
| CN107058854A (en) * | 2017-03-13 | 2017-08-18 | 昆明理工大学 | A kind of vacuum smelting method of the high manganese high-aluminum steel of Nb, V, Ti microalloying |
| CN108642403A (en) * | 2018-05-28 | 2018-10-12 | 河北工业大学 | A kind of 780MPa grade super strengths Fe-Mn-Al-C systems lightweight cast steel and preparation method thereof |
| CN108486506A (en) * | 2018-05-31 | 2018-09-04 | 中北大学 | A kind of preparation method and application of high-performance low-density steel plate |
Non-Patent Citations (3)
| Title |
|---|
| 吴志强等: "高强塑性低密度高锰钢TIG焊焊接头显微组织及力学性能", 《点焊机》 * |
| 罗翔: "Fe-28Mn-10Al-0.8C低密度高强钢组织与力学性能研究", 《中国优秀硕士学位论文全文数据库 工程科技Ⅰ辑》 * |
| 邱葭菲等: "《实用焊接技术 焊接方法工艺质量控制技能技巧与考证竞赛》", 31 October 2010, 湖南科学技术出版社 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114769938A (en) * | 2022-04-24 | 2022-07-22 | 燕山大学 | Metal flux-cored wire and preparation method and application thereof |
| CN114769938B (en) * | 2022-04-24 | 2023-07-04 | 燕山大学 | Metal flux-cored wire and preparation method and application thereof |
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