CN113046646A - High-strength low-density dual-phase steel and preparation method thereof - Google Patents

High-strength low-density dual-phase steel and preparation method thereof Download PDF

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CN113046646A
CN113046646A CN202110268145.XA CN202110268145A CN113046646A CN 113046646 A CN113046646 A CN 113046646A CN 202110268145 A CN202110268145 A CN 202110268145A CN 113046646 A CN113046646 A CN 113046646A
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steel
density
phase steel
hot rolling
dual
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刘日平
石鹤洋
马明臻
景勤
张新宇
王飞
张国峰
唐轶浩
王锁涛
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Yanshan University
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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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • 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
    • 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
    • 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
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • 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
    • 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
    • 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
    • C21D2211/005—Ferrite

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention provides high-strength low-density dual-phase steel, and belongs to the technical field of steel materials. In the dual-phase steel, Al is used as a strong ferrite stability element, and a large amount of ferrite structures appear in the steel due to the addition of Al; the Be element is also a strong ferrite stability element, but compared with the Al element, the Be element has smaller density, and the density of the steel can Be greatly reduced on the premise of ensuring the strength of the dual-phase steel in the alloying process; mn and C are strong austenite stability elements, and an austenite structure with better structure property can be obtained by adding Mn and C in steel; the elements of the invention cooperate with each other, so that the dual-phase steel has lower density while keeping higher strength. Compared with the existing Fe-Mn-Al-C steel, the high-strength low-density dual-phase steel provided by the invention basically keeps the same yield strength and tensile strength, and the density is reduced by 3.65-6.69%.

Description

High-strength low-density dual-phase steel and preparation method thereof
Technical Field
The invention relates to the technical field of steel materials, in particular to high-strength low-density dual-phase steel and a preparation method thereof.
Background
In recent years, the specific gravity of high-strength low-density steel has been increasing in military field, and the demand has been increasing. The weight reduction capability of the existing Fe-Mn-Al-C high-strength low-density steel is very limited only through the structural aspect (stressed component), and the service condition of lower density is difficult to meet. Therefore, how to further reduce the density of the material under the premise of ensuring the strength becomes a technical problem to be solved urgently.
Disclosure of Invention
The invention aims to provide high-strength low-density dual-phase steel and a preparation method thereof.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides high-strength low-density dual-phase steel which comprises the following elements in percentage by mass: 1.4-1.6% of C, 10-11% of Al, 30-35% of Mn, 1.0-2.5% of Be and the balance of Fe.
Preferably, the alloy comprises 1.5% of C, 10% of Al, 30% of Mn, 1.0-2.0% of Be and the balance of Fe.
The invention provides a preparation method of the high-strength low-density dual-phase steel, which comprises the following steps:
smelting and forging the raw materials consisting of the high-strength low-density dual-phase steel corresponding to the scheme to obtain an ingot;
and carrying out homogenization treatment, hot rolling and solution treatment on the cast ingot in sequence to obtain the high-strength low-density dual-phase steel.
Preferably, the smelting is carried out in a vacuum induction smelting furnace.
Preferably, the smelting process comprises the following steps: putting the raw materials into a vacuum induction smelting furnace from bottom to top in sequence according to the sequence of melting points from low to high, vacuumizing the vacuum induction smelting furnace, filling argon into the vacuumized furnace body, smelting under the stirring condition, preserving the heat for 15-20 min when the surface of the molten steel is completely dissolved to be clear until no obvious suspended matters exist, pouring the molten steel into a mold, and cooling.
Preferably, the homogenization treatment temperature is the same as the hot rolling temperature.
Preferably, the temperature of the homogenization treatment is 1050-1250 ℃, and the heat preservation time is 2-5 h
Preferably, the hot rolling is multi-pass hot rolling, the total deformation of the hot rolling is 60-65%, and the deformation of each pass is 1.35-2 mm.
Preferably, the heat preservation treatment is carried out on the blank obtained after the previous hot rolling in the adjacent hot rolling passes, the temperature of the heat preservation treatment is the same as that of the next hot rolling pass, and the time of the heat preservation treatment is 5-10 min.
Preferably, the temperature of the solution treatment is 1050-1250 ℃, and the heat preservation time is 60-120 min.
The invention provides high-strength low-density dual-phase steel which comprises the following elements in percentage by mass: 1.4-1.6% of C, 10-11% of Al, 30-35% of Mn, 1.0-2.5% of Be and the balance of Fe. In the dual-phase steel, Al is used as a strong ferrite stability element, and a large amount of ferrite structures appear in the steel due to the addition of Al; the Be element is also a strong ferrite stability element, but compared with the Al element, the Be element has smaller density, and the density of the steel can Be greatly reduced on the premise of ensuring the strength of the dual-phase steel in the alloying process; mn and C are strong austenite stability elements, and an austenite structure with better structure property can be obtained by adding Mn and C in steel; the elements of the invention cooperate with each other, so that the dual-phase steel has lower density while keeping higher strength.
The results of the examples show that the yield strength and the tensile strength of the high-strength low-density dual-phase steel are basically consistent and the density is reduced by 3.65-6.69% compared with the existing Fe-Mn-Al-C steel.
Drawings
FIG. 1 is a plot of tensile specimen dimensions in units: mm;
FIG. 2 is a metallographic optical micrograph of a high strength low density dual phase steel prepared according to example 1;
FIG. 3 is a metallographic optical micrograph of a high strength low density dual phase steel prepared in example 2.
Detailed Description
The invention provides high-strength low-density dual-phase steel which comprises the following elements in percentage by mass: 1.4-1.6% of C, 10-11% of Al, 30-35% of Mn, 1.0-2.5% of Be and the balance of Fe.
The high-strength low-density dual-phase steel provided by the invention comprises 1.4-1.6% of C, preferably 1.45-1.55% of C, and more preferably 1.5% of C by mass percentage.
The high-strength low-density dual-phase steel provided by the invention comprises 10-11% of Al, preferably 10.2-10.8%, and more preferably 10.4-10.6% in percentage by mass.
The high-strength low-density dual-phase steel provided by the invention comprises 30-35% of Mn, preferably 31-34% of Mn, and more preferably 32-33% of Mn in percentage by mass.
The high-strength low-density dual-phase steel provided by the invention comprises, by mass, 1.0-2.5% of Be, preferably 1.0-2.0%, and more preferably 1.2-1.8%.
The high-strength low-density dual-phase steel provided by the invention comprises the balance of Fe and other inevitable impurities in percentage by mass.
In the invention, Al is used as a strong ferrite stability element, and a large amount of ferrite tissues appear in the steel due to the addition of Al; the Be element is also a strong ferrite stability element, but compared with the Al element, the Be element has smaller density, and the density of the steel can Be greatly reduced on the premise of ensuring the strength and the plasticity of the dual-phase steel in the alloying process; mn and C are strong austenite stability elements, and an austenite structure with better structure property can be obtained by adding Mn and C in steel; the elements of the invention cooperate with each other, so that the dual-phase steel has lower density while keeping higher strength.
The invention provides a preparation method of the high-strength low-density dual-phase steel, which comprises the following steps:
smelting and forging the raw materials consisting of the high-strength low-density dual-phase steel corresponding to the scheme to obtain an ingot;
and carrying out homogenization treatment, hot rolling and solution treatment on the cast ingot in sequence to obtain the high-strength low-density dual-phase steel.
The invention melts and forges the raw materials which are composed of the high-strength low-density dual-phase steel corresponding to the scheme to obtain the ingot. In the present invention, the raw materials are preferably used in the form of a simple substance. In the present invention, the raw material preferably includes carbon, electrolytic manganese flakes, aluminum, beryllium, and commercially pure iron.
Before smelting, the invention preferably also comprises cleaning each raw material. In the present invention, the cleaning method is preferably: the raw materials are firstly cleaned by ultrasonic wave in acetone and then cleaned by ultrasonic wave in alcohol. The present invention has no special requirement on the ultrasonic cleaning conditions, and the ultrasonic cleaning conditions known in the art can be adopted.
In the present invention, the melting is preferably performed in a vacuum induction melting furnace. The invention carries out smelting in the vacuum induction smelting furnace, and omits the procedures of deoxidization, slag removal and the like.
In the present invention, the smelting process is preferably: putting the raw materials into a vacuum induction smelting furnace from bottom to top in sequence according to the sequence of melting points from low to high, vacuumizing the vacuum induction smelting furnace, filling argon into the vacuumized furnace body, smelting under the stirring condition, preserving the heat for 15-20 min when the surface of the molten steel is completely dissolved to be clear until no obvious suspended matters exist, pouring the molten steel into a mold, and cooling.
The invention is preferably vacuumized to 2X 10-2Pa or less. The invention has no special requirement on the smelting temperature, and the proper smelting temperature can be determined according to the common knowledge in the field. According to the invention, all raw materials are sequentially put into a vacuum induction melting furnace from bottom to top according to the sequence of melting points from low to high, the raw material with high melting point is put above and firstly contacted with a welding gun and can ensure that the temperature of the raw material reaches the melting standard of the metal simple substance, and the raw material with low melting point can ensure complete melting under the condition that the melting point of the raw material is higher than the self melting point.
The invention preferably adopts multiple times of smelting, thereby being beneficial to obtaining the ingot with uniform components. The number of the melting is preferably 6.
After the smelting is finished, the invention forges the smelted steel to obtain an ingot.
In the invention, the forging temperature is preferably 1080-1280 ℃, and more preferably 1100-1200 ℃. In the present invention, the rate of temperature increase to the temperature for forging is preferably 10 ℃/min. In the invention, after forging, the obtained forged block is preferably returned to the furnace and kept warm for 30min, and the ingot is obtained after water cooling to room temperature. The invention keeps the temperature in a controlled range during water cooling by returning to the furnace for heat preservation, thereby avoiding that the preset temperature can not be reached because of heat loss in the forging process. The invention obtains the ingot with the expected shape by forging.
After obtaining the ingot, the invention carries out homogenization treatment, hot rolling and solution treatment on the ingot in sequence to obtain the high-strength low-density dual-phase steel.
In the present invention, the temperature of the homogenization treatment is preferably the same as the temperature of hot rolling; the temperature of the homogenization treatment is preferably 1050-1250 ℃, and more preferably 1100-1200 ℃; the heat preservation time is preferably 2-5 h, and more preferably 2-3 h. In the present invention, the rate of temperature increase to the temperature of the homogenization treatment is preferably 10 ℃/min. The invention ensures the internal organization of the material to be uniform by utilizing homogenization treatment.
After the homogenization treatment is finished, the obtained homogenized cast ingot is subjected to hot rolling. In the present invention, the hot rolling is preferably multi-pass hot rolling. When multiple passes of hot rolling are employed, the temperature of each pass is preferably the same. In the invention, the total deformation of the hot rolling is preferably 60-65%, and more preferably 62-64%; the deformation amount of each pass is preferably 1.35-2 mm. In the present invention, the hot rolling is preferably performed in a twin roll mill.
In the invention, between adjacent hot rolling passes, preferably, the heat preservation treatment is carried out on the blank obtained after the last hot rolling pass, the temperature of the heat preservation treatment is the same as that of hot rolling, and the time of the heat preservation treatment is preferably 5-10 min. The invention can keep the microstructure state of the blank after each pass of rolling deformation as much as possible by carrying out heat preservation treatment, increases the density of the grain boundary and improves the strong plasticity.
After the hot rolling is finished, the obtained plate is subjected to solution treatment. In the invention, the temperature of the solution treatment is preferably 1050-1250 ℃, and the heat preservation time is preferably 60-120 min, and more preferably 80-100 min. In the present invention, the cooling method of the solution treatment is preferably water quenching; the temperature of water used for water quenching is preferably room temperature. The supersaturated solid solution is obtained through solution treatment, and the strength of the dual-phase steel is improved. After the solution treatment is completed, the oxide skin on the surface of the obtained plate is preferably polished and cleaned, so that the high-strength low-density dual-phase steel is obtained.
The high-strength low-density dual-phase steel provided by the present invention will be described in detail with reference to examples, but they should not be construed as limiting the scope of the present invention.
Example 1
The dual-phase steel of the embodiment comprises the following components in percentage by mass: 57.5 percent of Fe, 30 percent of Mn, 10 percent of Al, 1.5 percent of C and 1.0 percent of Be.
According to parts by weight, 1.50 parts of carbon, 30.0 parts of electrolytic manganese sheet, 10.0 parts of aluminum, 1.0 part of beryllium and 57.5 parts of industrial pure iron are taken. Putting the raw materials into a crucible of a vacuum induction melting furnace from bottom to top in sequence according to the sequence of melting points from low to high, wherein the vacuum degree in the furnace cavity is 2 multiplied by 10-2Below Pa, introducing high-purity argon as a protective gas before smelting, adding magnetic stirring to uniformly mix the high-purity argon, pouring the molten steel into a mold prepared in advance after the surface of the molten steel is completely dissolved and clear until no obvious suspended matters exist, preserving heat for 20min, heating the alloy to the forging temperature (1050 ℃) at the speed of 10 ℃/min to forge the alloy after the alloy is completely cooled, returning the forging block to the furnace after forging, preserving heat for 30min, cooling the forging block by water, and cutting the forging block completely cooled to room temperature into 20 multiplied by 30 multiplied by 50cm ingots by wire cutting; heating the cast ingot to 1150 ℃ at the speed of 10 ℃/min, preserving heat for 2h, carrying out homogenization treatment, then carrying out hot rolling at 1050 ℃, wherein the hot rolling is multi-pass hot rolling, the reduction of each pass is 2mm, after each pass of rolling, putting the sample into a muffle furnace, reheating to 1050 ℃, preserving heat for 10min, carrying out heat preservation treatment, and finally rolling the cast ingot into a plate with the thickness of 5mm, wherein the final deformation is 60%. And (3) reheating the obtained plate to 1050 ℃, preserving heat for 30min for solid solution treatment, then rapidly performing water quenching in room-temperature water, cooling to the ambient temperature, taking out the plate after the plate is completely cooled, polishing off oxide skin on the surface, and cleaning the oxide skin to obtain the high-strength low-density dual-phase steel.
Example 2
The dual-phase steel of the embodiment is different from the dual-phase steel of the embodiment 1 only in that the dual-phase steel of the embodiment comprises the following components in percentage by mass: 56.5 percent of Fe, 30 percent of Mn, 10 percent of Al, 1.5 percent of C and 2.0 percent of Be. The preparation method is the same as example 1.
Comparative example 1
The Fe-Mn-Al-C type high-strength low-density steel is prepared from the following chemical components in percentage by mass: 30% of manganese, 10% of aluminum, 1.25% of carbon and 58.75% of industrial pure iron. The preparation method is the same as example 1.
Structure and performance
1. Metallographic structure observation was performed on the high-strength low-density dual-phase steel prepared in example 1, and the results are shown in fig. 2. As can be seen from fig. 2, the high-strength low-density dual-phase steel obtained in example 1 had a metallographic phase mainly containing an austenite phase.
2. Metallographic structure observation was performed on the high-strength low-density dual-phase steel prepared in example 2, and the results are shown in fig. 3. As can be seen from FIG. 3, the metallographic phase of the high-strength low-density dual-phase steel obtained in example 2 was mainly in the austenite phase
3. Tensile test was performed by cutting out the low density steels prepared in examples 1 to 2 and comparative example 1 into tensile test pieces as shown in FIG. 1 by wire cutting, 3 tensile test pieces were cut out from each dual phase steel to ensure reproducibility of the tensile test results, and uniaxial tensile test was performed using a universal material testing machine model Instron5982 with a tensile rate set at 5X 10-4s-1The data thus obtained relating to the mechanical properties are shown in table 1. 10X 5mm cubes are taken from the rolled steel plate by linear cutting, the density is measured by the Archimedes principle, each alloy plate is positioned at different positions, and three blocks are taken to ensure the accuracy and repeatability of the result. The test results are shown in Table 1.
TABLE 1 Performance data for the example and comparative low density steels
Figure BDA0002972894840000061
As can be seen from Table 1, the yield strength and tensile strength of the high-strength dual-phase steel prepared by the invention are basically consistent with those of Fe-Mn-Al-C type low-density steel (comparative example 1), but the density is greatly reduced, and the reduction amount reaches 3.65-6.69%.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.

Claims (10)

1. The high-strength low-density dual-phase steel is characterized by comprising the following elements in percentage by mass: 1.4-1.6% of C, 10-11% of Al, 30-35% of Mn, 1.0-2.5% of Be and the balance of Fe.
2. The high-strength low-density dual-phase steel according to claim 1, comprising C1.5%, Al 10%, Mn 30%, Be 1.0-2.0%, and the balance Fe.
3. A method of producing a high-strength low-density dual-phase steel according to claim 1 or 2, characterized by comprising the steps of:
smelting and forging a raw material consisting of the high-strength low-density dual-phase steel according to claim 1 or 2 to obtain an ingot;
and carrying out homogenization treatment, hot rolling and solution treatment on the cast ingot in sequence to obtain the high-strength low-density dual-phase steel.
4. The method of claim 3, wherein the melting is performed in a vacuum induction melting furnace.
5. The method of claim 4, wherein the smelting is performed by: putting the raw materials into a vacuum induction smelting furnace from bottom to top in sequence according to the sequence of melting points from low to high, vacuumizing the vacuum induction smelting furnace, filling argon into the vacuumized furnace body, smelting under the stirring condition, preserving the heat for 15-20 min when the surface of the molten steel is completely dissolved to be clear until no obvious suspended matters exist, pouring the molten steel into a mold, and cooling.
6. The production method according to claim 3, wherein the temperature of the homogenization treatment is the same as the temperature of the hot rolling.
7. The preparation method according to claim 6, wherein the homogenization treatment temperature is 1050-1250 ℃ and the holding time is 2-5 h.
8. The preparation method according to claim 3, wherein the hot rolling is multi-pass hot rolling, the total deformation of the hot rolling is 60-65%, and the deformation of each pass is 1.35-2 mm.
9. The preparation method of the steel plate blank according to claim 8, wherein the adjacent hot rolling passes further comprise a heat preservation treatment of the blank obtained after the previous hot rolling pass, the temperature of the heat preservation treatment is the same as that of the next hot rolling pass, and the time of the heat preservation treatment is 5-10 min.
10. The production method according to claim 3, wherein the temperature of the solution treatment is 1050 to 1250 ℃ and the holding time is 60 to 120 min.
CN202110268145.XA 2021-03-12 2021-03-12 High-strength low-density dual-phase steel and preparation method thereof Withdrawn CN113046646A (en)

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113737105A (en) * 2021-09-07 2021-12-03 燕山大学 Rare earth-containing weathering steel and preparation method thereof
CN115821168A (en) * 2022-12-20 2023-03-21 燕山大学 Low-density high-wear-resistance alloy steel and preparation method thereof

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113737105A (en) * 2021-09-07 2021-12-03 燕山大学 Rare earth-containing weathering steel and preparation method thereof
CN115821168A (en) * 2022-12-20 2023-03-21 燕山大学 Low-density high-wear-resistance alloy steel and preparation method thereof

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