CN108474082A - The high manganese steel sheet and its manufacturing method of vibrationproof excellent - Google Patents
The high manganese steel sheet and its manufacturing method of vibrationproof excellent Download PDFInfo
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- CN108474082A CN108474082A CN201680075456.1A CN201680075456A CN108474082A CN 108474082 A CN108474082 A CN 108474082A CN 201680075456 A CN201680075456 A CN 201680075456A CN 108474082 A CN108474082 A CN 108474082A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention relates to high manganese steel sheet and its manufacturing methods, and in terms of weight %, the steel plate includes：C：0~0.1% or less, Mn：8~30%, P：0.1% or less, S：0.02% or less, N：0.1% or less, Ti：0~1.0% and Fe and inevitable impurity, microstructure are made of ε martensites and austenite, and the average grain diameter of martensite and austenite is 2 μm or less.
Description
Technical field
The present invention relates to the high manganese steel sheet of vibrationproof excellent, the steel plate can be made into automobile or steel plate for building,
So as to be used in the place for the vibrationproof characteristic for needing to reduce noise.
Background technology
In recent years, for automobile making and construction material, it is that manufacturer has to solve the problems, such as to reduce noise.Just
For automaker, the especially needed excellent machinery on generating the structural members such as engine portion, the oil sump of prodigious noise
Characteristic and vibrationproof characteristic.For construction material, in recent years, due to the reinforcement of interlayer noise control, as including apartment
Tier building floor need develop vibration damping sheet.
High manganese vibrationproof steel is so that noise energy is converted to thermal energy by the interface sliding of ε martensites when by external impact
And the steel grade with high vibrationproof characteristic and excellent engineering properties, therefore it is suitable for purpose as described above.
Invention content
Technical problems to be solved
The object of the present invention is to provide the high manganese steel sheet of vibrationproof excellent and its manufacturing methods.
Technical solution
The preferred high manganese steel sheet for being related to vibrationproof excellent on one side of the present invention, in terms of weight %, the steel plate
Including：C：0~0.1% or less, Mn：8~30%, P：0.1% or less, S：0.02% or less, N：0.1% or less, Ti：0~
1.0% and Fe and inevitable impurity, microstructure are made of ε martensites and austenite, and martensite and austenite are averaged
Grain size is 2 μm or less.
In addition, the method for the preferred high manganese steel sheet for being related to manufacturing vibrationproof excellent on the other hand of the present invention, institute
The method of stating includes the following steps：With 0.01~200 DEG C/sec of heating rate, heating meets the steel plate of above-mentioned compositing range to Ac1
~Ac3+50 DEG C of heat treatment temperature；It is maintained 0.01 second~24 hours under the heat treatment temperature；And with 0.01 DEG C/sec with
On cooling velocity be cooled to room temperature.
Advantageous effect
The present invention is capable of providing the high manganese steel sheet of vibrationproof excellent, therefore can be used in the automobile for needing to eliminate noise
With structure member and the flooring material etc. of construction material.
Description of the drawings
Fig. 1 is the embodiment for showing to be heat-treated at 600 DEG C and the comparison that is heat-treated at 700~1000 DEG C
The figure of the microstructure of example.
Fig. 2 is the figure in the dilatometer period (cycle) for showing to be heat-treated shown in Fig. 1.
Fig. 3 is specific damping capacity (the Specific Damping that Examples and Comparative Examples (4) are measured by internal resistance method
Capacity, SDC) result chart.
Preferred forms
In the following, the present invention is described in detail.
The present invention relates to the high manganese steel sheet of vibrationproof excellent and its manufacturing methods, and in terms of weight %, the steel plate includes：
C：0~0.1% or less, Mn：8~30%, P：0.1% or less (including 0%), S：0.02% or less (including 0%), N：0.1%
(including 0%), Ti below：1.0% or less (except 0) and Fe and inevitable impurity, microstructure is by ε martensites and Ovshinsky
Body forms, and the average grain diameter of martensite and austenite is 2 μm or less.
The reasons why specific steel of the steel plate of the present invention is formed and limited its ingredient is as follows.
For C, when the additive amount of C is more than 0.1%, excessive carbide can be precipitated, to reduce hot-workability and
Elongation percentage, and vibrationproof ability is greatly reduced, therefore the additive amount of C is limited to 0.1% or less.
Mn is the element for steadily ensuring the essential elements of austenite structure, and being raising stacking fault energy, when Mn's
When additive amount is less than 8%, due to forming the martensite of damage mouldability, although intensity can increase, ductility can drastically drop
It is low.Also, stacking fault energy can reduce, and also be easy mutually to become ε martensites to be formed by a part of austenite, therefore Mn
Lower limit is limited to 8%.On the other hand, when the additive amount of Mn is more than 30%, the increasing of manufacturing cost is caused due to a large amount of manganese
Add, and due to the increase of phosphorus (P) content in steel cracks as slab.In addition, the additive amount of Mn more increases
Add, excessive inside grain boundary oxidation is more will produce when being reheated to slab, to cause defect oxide in surface of steel plate,
And when carrying out galvanizing by dipping, surface characteristic can also be deteriorated, therefore the upper limit of the additive amount of Mn is limited to 30%.
Phosphorus (P) and sulphur (S) are to manufacture the element inevitably contained when steel, therefore the content of phosphorus (P) is preferably limited to
The content of 0.1% or less (including 0%), sulphur (S) is preferably limited to 0.02% or less (including 0%).In particular, phosphorus will produce partially
Analysis, to reduce the processability of steel, sulphur can form coarse manganese sulfide (MnS), the defects of so as to cause flange crack, and reduce
The hole expandability of steel plate, it is therefore desirable to inhibit the additive amount of p and s to the maximum extent.
The element that inevitably contains when nitrogen (N) is manufacture, thus preferably by the addition scope limitation of N be 0.1% with
Under (including 0%).
Titanium (Ti) is to be combined to form the carbide of carbide with carbon, and being at this moment formed by carbide can hinder
The growth of crystal grain, therefore Ti is the effective element of miniaturization to grain size number.Also, when compound addition titanium and boron, in column
High temperature compound is formed in brilliant crystal boundary, to prevent grain-boundary crack.In addition, forming compound with C, N, it is reduced to have
Score removal (Scavenging) effect, therefore Ti be to improve vibrationproof ability necessary element.But when Ti's
When content is more than 1.00%, excessive titanium segregation becomes excessively coarse in crystal boundary, so as to cause embrittlement of grain boundaries or precipitated phase
Change, to reduce the growth result of crystal grain, therefore the additive amount of titanium is limited to 1.0% or less.
In terms of weight %, the potassium steel of another aspect of the present invention can further include：Si：0~3%, Cr：
0.005%~5.0%, Ni：0.005~2.0%, Nb：0.005~0.5%, B：0.0001~0.01%, V：0.005~
0.5% and W：One or more of 0.005~1%.
Silicon (Si) is solution strengthening element, and is the member for increasing yield strength by solid solution effect reduction grain size number
Element, in order to ensure intensity needs to add silicon.But it when increasing the additive amount of silicon, is formed on surface of steel plate when carrying out hot rolling
Si oxide to make pickling be deteriorated, therefore has the shortcomings that the poor surface quality for making steel plate.Moreover, it is adding
When a large amount of silicon, the weldability of steel can be greatly reduced.Therefore, the upper limit of the additive amount of silicon can be limited to 3%.
For Cr, carrying out hot rolling or when annealing operation, Cr reacted with the oxygen of outside and on surface of steel plate preferential shape
The Cr systems oxidation film (Cr for being 20~50 μm at thickness2O3), to prevent the dissolutions such as Mn, Si for including in steel to surface layer, thus have
Help the stabilisation of textura epidermoidea, and can play the role of improving the element of coating surface characteristic.
But when the content of Cr is less than 0.005%, said effect is small, when the content of Cr is more than 5.0%, is formed
Chromium carbide, to reduce processability and delayed fracture resistance characteristics, therefore the upper limit of Cr contents can be limited to 5.0%.
Ni not only facilitates the stabilisation of austenite and is conducive to improve elongation percentage, and especially contributes effectively to carry
The element of high high-temperature ductility.Ni is the strong element for improving high temperature toughness, right when the content of Ni is less than 0.005%
The effect of high temperature toughness is very small, and the additive amount of Ni more increases, and can be shown to preventing delayed fracture resistance and slab crackle more
Show apparent effect, it is still, of high cost due to material, cause production cost to rise, therefore the content of Ni can be limited to
0.005~2.0%.
Nb is to be combined to form the carbide former of carbide with the carbon in steel, the present invention in can with improve intensity and
The purpose of granularity miniaturization adds Nb.Usual Nb forms precipitated phase at a temperature of less than Ti, therefore Nb is crystallite dimension
The big element of precipitating reinforcing effect, can add 0.005~0.5% Nb caused by miniaturization and the formation of precipitated phase.But
It is that, when the additive amount of Nb is less than 0.005%, effect is small, it is on the other hand, excessive when the additive amount of Nb is more than 0.5%
Nb be segregated in crystal boundary, become excessively coarsening so as to cause embrittlement of grain boundaries or precipitated phase, to reduce the growth of crystal grain
Effect, and delay to recrystallize in hot-rolled process, to increase rolling loading, therefore the additive amount of Nb can be limited to
0.005~0.5%.
As Ti, V and W are to be combined to form the element of carbonitride with C, N, V and W is formed fine at low temperature in the present invention
Precipitated phase, therefore can have precipitating reinforcing effect, and can be for ensuring that the important element of austenite.But
When with micro addition V and W less than 0.005%, effect is small, on the other hand, when the additive amount of V is more than the addition of 0.5%, W
When amount is more than 1.0%, precipitated phase becomes excessively coarsening, to reduce the growth result of crystal grain, and can become hot short
Reason, therefore the additive amount of V can be limited to the additive amount of 0.005~0.5%, W can be limited to 0.005~1%.
Boron (B) can add together with Ti and be formed the high temperature compound of crystal boundary, so as to prevent grain-boundary crack.But
It is when with 0.0001% micro addition B below, without effect, when the additive amount of B is more than 0.01%, to form boron compound,
To make surface characteristic be deteriorated, therefore the range of boron can be limited to 0.0001~0.01%.
In the following, being illustrated to the method for the high manganese steel sheet of the manufacture vibrationproof excellent of the present invention.
In the method for the manufacture high manganese steel sheet of the present invention, with 0.01~200 DEG C/sec of heating rate, heating has above-mentioned
The steel that ingredient and composition range and microstructure are made of austenite main phase, and under Ac1~Ac3+50 DEG C of heat treatment temperature
After maintaining 0.01 second~24 hours, it is cooled to room temperature with 0.01 DEG C/sec or more of cooling velocity.
The high manganese steel sheet can be cold-rolled steel sheet or hot rolled steel plate.
The microstructure of the high manganese steel sheet is made of ε martensites and austenite.
When in the heating stepses being more than 200 DEG C/sec, Ac1 and Ac3 temperature can rise, even if to the present invention's
Condition and range is heat-treated, and can also there are problems that the average grain diameter of microstructure is more than 2 μm, therefore the upper limit of heating rate
It is limited to 200 DEG C/sec.It is unstable due to phase when being operated with 0.01 DEG C/sec of heating rate below, it can generate coarse
Carbide, it is therefore desirable to be heat-treated with 0.01 DEG C/sec of speed below.
When carrying out the heat treatment with the temperature less than Ac1, phase transformation will not be carried out, is not in heat treatment to exist
The problem of effect, has that the average grain diameter of microstructure is more than 2 μm when heat treatment temperature is more than Ac3+50 DEG C, because
This needs heat treatment temperature being limited to Ac1~Ac3+50 DEG C.
When the heat treatment time is less than 0.01 second, recrystallization and recovery effects are small, from without being heat-treated
Effect generates excessive oxidation when the heat treatment time is more than 24 hours, to existence foundation iron be corroded and disappear and
The technological problems of excessive heat treatment cost are consumed, and the average grain diameter of the microstructure grown is more than desired average
The problem of grain size.
When being cooled down with the cooling velocity less than 0.01 DEG C/sec in the cooling step, during cooling not
Only the average grain diameter of microstructure can become larger, but also there are problems that because phase it is unstable due to generate coarse carbide, because
The lower limit of this cooling velocity is 0.01 DEG C/sec.The upper limit is not provided with for cooling velocity, cooling velocity is faster, is more conducive to
Ensure ε martensites and fine average grain diameter.
Specific implementation mode
In the following, the embodiment of the present invention is described in detail.Embodiment below is only used for understanding the present invention, and unlimited
The fixed present invention.
Cold-rolled steel sheet is heated with 5 DEG C/sec of heating rate, and under heat treatment temperature as described in Table 1, in Re Chu
It is maintained during the reason period, is then cooled to room temperature with 5 DEG C/sec of cooling velocity, in terms of weight %, the cold rolling
Steel plate includes：C：0.02%, Mn：17%, N：0.01、P：0.008、S：0.008%, Ti：0.03% and Fe and inevitably
Impurity.
For the steel plate for being heat-treated and being cooled down as described above, the average grain diameter and ε martensites of microstructure are investigated
Score, and the results are shown in following table 1 and Fig. 1.
[table 1]
| It distinguishes | Heat treatment temperature (DEG C) | Heat treatment time (minute) | Grain size (μm) | The area fraction (%) of ε martensites |
| Embodiment | 600 | 30 | 1.23 | 6.2 |
| Comparative example 1 | 700 | 30 | 2.3 | 3 |
| Comparative example 2 | 800 | 30 | 3.6 | 14.9 |
| Comparative example 3 | 900 | 10 | 6.7 | 16.8 |
| Comparative example 4 | 1000 | 30 | 6.7 | 34.6 |
As shown in the table 1 and Fig. 1, compare the embodiment being heat-treated at 600 DEG C and at 700~1000 DEG C
The comparative example (1-4) that is heat-treated is it is recognised that compared with the embodiment being heat-treated at 600 DEG C, heat treatment temperature
Area fraction for the ε martensites of 700 DEG C of comparative examples (1) is lower and grain size bigger.
In addition, heat treatment temperature is respectively the area of the ε martensites of 800 DEG C, 900 DEG C and 1000 DEG C of comparative example (2-4)
Score is more than the embodiment being heat-treated at 600 DEG C, but the grain size for the embodiment being heat-treated at 600 DEG C is less than
The grain size for the comparative example (2-4) being heat-treated at 700~1000 DEG C.
Furthermore it is possible to know the average grain diameter of the microstructure for the embodiment of the present invention being heat-treated at 600 DEG C
It is 2 μm or less.
Fig. 2 is the figure in the dilatometer period for showing to be heat-treated shown in Fig. 1.
It can be confirmed that Ac1 and Ac3, embodiment are the results being heat-treated at Ac3+30 DEG C by Fig. 2.
Fig. 3 shows to measure the embodiment being heat-treated at 600 DEG C by friction coefficient method and be carried out at 1000 DEG C
The result of the specific damping capacity (Specific Damping Capacity, SDC) of the comparative example (4) of heat treatment.
Wherein, SDC indicates damping capacity (object absorbs the property of vibration).
Referring to Figure 1 and Figure 3 it is recognised that compared with the vibrationproof steel of comparative example (4), has and be heat-treated at 600 DEG C
Embodiment microstructure vibrationproof steel room temperature SDC values have high 2.5 times of value.That is, measured carry out at 600 DEG C
The SDC values of the embodiment of heat treatment are 0.00025, the SDC values of the measured comparative example (4) being heat-treated at 1000 DEG C
It is 0.0001.
The area fraction of the ε martensites for the embodiment being heat-treated at 600 DEG C is relatively low, but grain size is small, therefore
It organizes fine and is evenly distributed, to be applied in external punching together with ε martensites in remaining dislocation (dislocation) and interface
When hitting, the ratio for converting energy into thermal energy is improved, to help to improve damping capacity, therefore vibrationproof excellent.
In general, when room temperature SDC values are 0.00015 or more, it is believed that vibrationproof excellent.
In summary result according to the present invention it is recognised that when being heat-treated, it can be ensured that 2 μm of average grains below
Diameter, so as to ensure excellent vibrationproof characteristic.
For comparative example, other than the comparative example being heat-treated at 700 DEG C, although the Line Integral of ε martensites
Number is higher than embodiment, but the average grain diameter of microstructure is big, therefore vibrationproof poor performance.
Claims (6)
1. high manganese steel sheet, in terms of weight %, it includes：C：0.1% or less, Mn：8~30%, P：0.1% or less, S：0.02%
Below, N：0.1% or less, Ti：0~1.0% and Fe and inevitable impurity, microstructure is by ε martensites and austenite group
At the average grain diameter of martensite and austenite is 2 μm or less.
2. the high manganese steel sheet of vibrationproof excellent according to claim 1, which is characterized in that in terms of weight %, the steel
Plate further includes：Si：0~3%, Cr：0.005%~5.0%, Ni：0.005~2.0%, Nb：0.005~0.5%, B：
0.0001~0.01%, V：0.005~0.5% and W：One or more of 0.005~1%.
3. the high manganese steel sheet of vibrationproof excellent according to claim 1, which is characterized in that the room temperature SDC of the steel plate
Value is 0.00015 or more.
4. the method for manufacturing the high manganese steel sheet of vibrationproof excellent comprising following steps：
With 0.01~200 DEG C/sec of heating rate, the heat treatment temperature of high manganese steel sheet to Ac1~Ac3+50 DEG C is heated, with weight
% meters are measured, the high manganese steel sheet includes：C：0~0.1% or less, Mn：8~30%, P：0.1% or less, S：0.02% or less, N：
0.1% or less, Ti：0~1.0% and Fe and inevitable impurity；
It is maintained 0.01 second~24 hours under the heat treatment temperature；And
It is cooled to room temperature with 0.01 DEG C/sec or more of cooling velocity.
5. the method for the high manganese steel sheet of manufacture vibrationproof excellent according to claim 4, which is characterized in that the Gao Meng
The microstructure of steel plate is made of ε martensites and austenite.
6. the method for the high manganese steel sheet of manufacture vibrationproof excellent according to claim 4, which is characterized in that with weight %
Meter, the steel plate further include：Si：0~3%, Cr：0.005%~5.0%, Ni：0.005~2.0%, Nb：0.005~
0.5%, B：0.0001~0.01%, V：0.005~0.5% and W：One or more of 0.005~1%.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020150185471A KR101736636B1 (en) | 2015-12-23 | 2015-12-23 | HIHG-Mn STEEL PLATE HAVING EXCELLENT DAMPING PROPERTY AND METHOD FOR PRODUCING THE SAME |
| KR10-2015-0185471 | 2015-12-23 | ||
| PCT/KR2016/015040 WO2017111473A1 (en) | 2015-12-23 | 2016-12-21 | High manganese steel sheet having excellent vibration-proof property, and manufacturing method therefor |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN108474082A true CN108474082A (en) | 2018-08-31 |
| CN108474082B CN108474082B (en) | 2020-06-02 |
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ID=59048542
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201680075456.1A Active CN108474082B (en) | 2015-12-23 | 2016-12-21 | High manganese steel sheet having excellent vibration-proof properties and method for producing same |
Country Status (6)
| Country | Link |
|---|---|
| US (1) | US20180371586A1 (en) |
| EP (1) | EP3395978B1 (en) |
| JP (1) | JP2019504208A (en) |
| KR (1) | KR101736636B1 (en) |
| CN (1) | CN108474082B (en) |
| WO (1) | WO2017111473A1 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112840042A (en) * | 2018-10-18 | 2021-05-25 | Posco公司 | Method for manufacturing high manganese steel material having excellent shock resistance and formability, and high manganese steel material manufactured by the method |
| CN112899577A (en) * | 2021-01-18 | 2021-06-04 | 北京科技大学 | Preparation method of Fe-Mn series high-strength high-damping alloy |
| CN116334477A (en) * | 2023-01-09 | 2023-06-27 | 鞍钢股份有限公司 | Vibration-damping high manganese steel and manufacturing method thereof |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107794357B (en) * | 2017-10-26 | 2018-09-14 | 北京科技大学 | The method of super rapid heating technique productions superhigh intensity martensite cold-rolled steel sheet |
| CN114774800B (en) * | 2022-04-19 | 2023-08-08 | 河南科技大学 | Ultrahigh-strength high-plasticity and toughness martensitic steel and preparation method thereof |
Citations (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0741907A (en) * | 1993-07-28 | 1995-02-10 | Nippon Yakin Kogyo Co Ltd | Superplastic two-phase stainless steel |
| US5445685A (en) * | 1993-05-17 | 1995-08-29 | The Regents Of The University Of California | Transformation process for production of ultrahigh carbon steels and new alloys |
| CN1685071A (en) * | 2002-09-30 | 2005-10-19 | 株式会社那诺技术研究所 | Tenacious metallic nano-crystalline bulk material with high hardness and high strength, and its manufacturing method |
| CN101078091A (en) * | 2007-06-26 | 2007-11-28 | 郑州航空工业管理学院 | Casting high speed steel cutter and preparation method thereof |
| KR100840287B1 (en) * | 2006-12-26 | 2008-06-20 | 주식회사 포스코 | Composite steel of retained austenite and hcp martensite, and method for heat treatment thereof |
| CN102277539A (en) * | 2011-08-01 | 2011-12-14 | 南京钢铁股份有限公司 | High-strength steel with low yield ratio, high plasticity and ultrafine grain and preparation method thereof |
| CN102753717A (en) * | 2009-12-01 | 2012-10-24 | 新日铁住金不锈钢株式会社 | Fine grained austenitic stainless steel sheet exhibiting excellent stress corrosion cracking resistance and processability |
| CN103774050A (en) * | 2012-10-25 | 2014-05-07 | 吴雪 | High-ductility steel with low yield ratio |
| CN103774052A (en) * | 2012-10-25 | 2014-05-07 | 吴雪 | Method for preparing high-strength steel plate with thickness of 20 mm |
| CN103774051A (en) * | 2012-10-25 | 2014-05-07 | 吴雪 | High-strength steel |
| CN103917681A (en) * | 2011-11-07 | 2014-07-09 | Posco公司 | Steel sheet for hot press forming, hot press forming member, and manufacturing method thereof |
| CN103966506A (en) * | 2014-05-09 | 2014-08-06 | 曹帅 | Iron-based damping alloy with high damping characteristic and preparation method thereof |
| WO2015060499A1 (en) * | 2013-10-23 | 2015-04-30 | 주식회사 포스코 | High-strength and high-manganese steel sheet having excellent vibration-proof properties and method for producing same |
| CN104884655A (en) * | 2012-12-27 | 2015-09-02 | Posco公司 | High-manganese wear resistant steel having excellent weldability and method for manufacturing same |
Family Cites Families (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR960006453B1 (en) * | 1993-10-22 | 1996-05-16 | 최종술 | Making method of vibration decrease alloy steel & the manufacturing process |
| US5891388A (en) * | 1997-11-13 | 1999-04-06 | Woojin Inc. | Fe-Mn vibration damping alloy steel having superior tensile strength and good corrosion resistance |
| JP3886881B2 (en) * | 2002-10-18 | 2007-02-28 | 日新製鋼株式会社 | High Mn austenitic steel sheet with excellent anti-elasticity |
| WO2006109919A1 (en) * | 2005-04-11 | 2006-10-19 | Korea Institute Of Science And Technology | High-strength damping alloys and low-noise diamond saw using the same |
| JP4529872B2 (en) * | 2005-11-04 | 2010-08-25 | 住友金属工業株式会社 | High Mn steel material and manufacturing method thereof |
| KR20110075611A (en) * | 2009-12-28 | 2011-07-06 | 주식회사 포스코 | Wear resistant steel |
| JP5041029B2 (en) * | 2010-04-30 | 2012-10-03 | 住友金属工業株式会社 | Method for producing high manganese steel |
| KR20140119216A (en) * | 2013-03-27 | 2014-10-10 | 주식회사 우진 | High manganese alloy and the manufacturing method for high manganese alloy |
| KR101536469B1 (en) * | 2013-12-24 | 2015-07-13 | 주식회사 포스코 | High manganese steel having excellent vibration damping ability and machinability |
| CN103898401B (en) * | 2014-04-11 | 2016-04-20 | 四川大学 | A kind of method improving high strength ferrimanganic base damping alloy damping capacity |
-
2015
- 2015-12-23 KR KR1020150185471A patent/KR101736636B1/en active IP Right Grant
-
2016
- 2016-12-21 JP JP2018532710A patent/JP2019504208A/en active Pending
- 2016-12-21 EP EP16879340.4A patent/EP3395978B1/en active Active
- 2016-12-21 CN CN201680075456.1A patent/CN108474082B/en active Active
- 2016-12-21 US US16/061,134 patent/US20180371586A1/en not_active Abandoned
- 2016-12-21 WO PCT/KR2016/015040 patent/WO2017111473A1/en active Application Filing
Patent Citations (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5445685A (en) * | 1993-05-17 | 1995-08-29 | The Regents Of The University Of California | Transformation process for production of ultrahigh carbon steels and new alloys |
| JPH0741907A (en) * | 1993-07-28 | 1995-02-10 | Nippon Yakin Kogyo Co Ltd | Superplastic two-phase stainless steel |
| CN1685071A (en) * | 2002-09-30 | 2005-10-19 | 株式会社那诺技术研究所 | Tenacious metallic nano-crystalline bulk material with high hardness and high strength, and its manufacturing method |
| KR100840287B1 (en) * | 2006-12-26 | 2008-06-20 | 주식회사 포스코 | Composite steel of retained austenite and hcp martensite, and method for heat treatment thereof |
| CN101078091A (en) * | 2007-06-26 | 2007-11-28 | 郑州航空工业管理学院 | Casting high speed steel cutter and preparation method thereof |
| CN102753717A (en) * | 2009-12-01 | 2012-10-24 | 新日铁住金不锈钢株式会社 | Fine grained austenitic stainless steel sheet exhibiting excellent stress corrosion cracking resistance and processability |
| CN102277539A (en) * | 2011-08-01 | 2011-12-14 | 南京钢铁股份有限公司 | High-strength steel with low yield ratio, high plasticity and ultrafine grain and preparation method thereof |
| CN103917681A (en) * | 2011-11-07 | 2014-07-09 | Posco公司 | Steel sheet for hot press forming, hot press forming member, and manufacturing method thereof |
| CN103774050A (en) * | 2012-10-25 | 2014-05-07 | 吴雪 | High-ductility steel with low yield ratio |
| CN103774052A (en) * | 2012-10-25 | 2014-05-07 | 吴雪 | Method for preparing high-strength steel plate with thickness of 20 mm |
| CN103774051A (en) * | 2012-10-25 | 2014-05-07 | 吴雪 | High-strength steel |
| CN104884655A (en) * | 2012-12-27 | 2015-09-02 | Posco公司 | High-manganese wear resistant steel having excellent weldability and method for manufacturing same |
| WO2015060499A1 (en) * | 2013-10-23 | 2015-04-30 | 주식회사 포스코 | High-strength and high-manganese steel sheet having excellent vibration-proof properties and method for producing same |
| CN103966506A (en) * | 2014-05-09 | 2014-08-06 | 曹帅 | Iron-based damping alloy with high damping characteristic and preparation method thereof |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112840042A (en) * | 2018-10-18 | 2021-05-25 | Posco公司 | Method for manufacturing high manganese steel material having excellent shock resistance and formability, and high manganese steel material manufactured by the method |
| CN112899577A (en) * | 2021-01-18 | 2021-06-04 | 北京科技大学 | Preparation method of Fe-Mn series high-strength high-damping alloy |
| CN112899577B (en) * | 2021-01-18 | 2021-12-24 | 北京科技大学 | Preparation method of Fe-Mn series high-strength high-damping alloy |
| CN116334477A (en) * | 2023-01-09 | 2023-06-27 | 鞍钢股份有限公司 | Vibration-damping high manganese steel and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| US20180371586A1 (en) | 2018-12-27 |
| CN108474082B (en) | 2020-06-02 |
| EP3395978A4 (en) | 2019-01-02 |
| EP3395978B1 (en) | 2020-12-16 |
| KR101736636B1 (en) | 2017-05-17 |
| WO2017111473A1 (en) | 2017-06-29 |
| JP2019504208A (en) | 2019-02-14 |
| EP3395978A1 (en) | 2018-10-31 |
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