CN117904543A - Superfine lamellar dual-phase high-strength and high-toughness low-density steel and preparation method thereof - Google Patents
Superfine lamellar dual-phase high-strength and high-toughness low-density steel and preparation method thereof Download PDFInfo
- Publication number
- CN117904543A CN117904543A CN202311808667.XA CN202311808667A CN117904543A CN 117904543 A CN117904543 A CN 117904543A CN 202311808667 A CN202311808667 A CN 202311808667A CN 117904543 A CN117904543 A CN 117904543A
- Authority
- CN
- China
- Prior art keywords
- strength
- dual
- lamellar
- phase high
- low
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 141
- 239000010959 steel Substances 0.000 title claims abstract description 141
- 238000002360 preparation method Methods 0.000 title abstract description 25
- 238000005242 forging Methods 0.000 claims abstract description 50
- 239000000463 material Substances 0.000 claims abstract description 30
- 238000005098 hot rolling Methods 0.000 claims abstract description 29
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 20
- 238000000137 annealing Methods 0.000 claims abstract description 17
- 238000000034 method Methods 0.000 claims abstract description 16
- 239000000126 substance Substances 0.000 claims description 26
- 238000005266 casting Methods 0.000 claims description 25
- 229910045601 alloy Inorganic materials 0.000 claims description 20
- 239000000956 alloy Substances 0.000 claims description 20
- 238000001816 cooling Methods 0.000 claims description 20
- 238000004321 preservation Methods 0.000 claims description 20
- 239000002994 raw material Substances 0.000 claims description 18
- 238000007711 solidification Methods 0.000 claims description 16
- 230000008023 solidification Effects 0.000 claims description 16
- 229910052799 carbon Inorganic materials 0.000 claims description 15
- 238000005096 rolling process Methods 0.000 claims description 13
- 239000012535 impurity Substances 0.000 claims description 11
- 239000000203 mixture Substances 0.000 claims description 10
- 230000009467 reduction Effects 0.000 claims description 10
- 238000010891 electric arc Methods 0.000 claims description 3
- 230000006698 induction Effects 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 claims description 2
- 229910052750 molybdenum Inorganic materials 0.000 claims description 2
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 230000009977 dual effect Effects 0.000 claims 4
- 238000005260 corrosion Methods 0.000 abstract description 10
- 230000007797 corrosion Effects 0.000 abstract description 10
- 230000008569 process Effects 0.000 abstract description 10
- 238000013461 design Methods 0.000 abstract description 6
- 229910000943 NiAl Inorganic materials 0.000 abstract description 5
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 abstract description 5
- 230000015572 biosynthetic process Effects 0.000 abstract description 5
- 239000007769 metal material Substances 0.000 abstract description 3
- 238000009826 distribution Methods 0.000 abstract description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 12
- 238000011161 development Methods 0.000 description 11
- 238000002844 melting Methods 0.000 description 11
- 230000008018 melting Effects 0.000 description 11
- 238000010791 quenching Methods 0.000 description 11
- 230000000171 quenching effect Effects 0.000 description 11
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 10
- 238000004590 computer program Methods 0.000 description 7
- 229910052786 argon Inorganic materials 0.000 description 6
- 238000010586 diagram Methods 0.000 description 6
- 238000012545 processing Methods 0.000 description 6
- 238000001878 scanning electron micrograph Methods 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 239000002131 composite material Substances 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 5
- 229910052742 iron Inorganic materials 0.000 description 5
- 238000005303 weighing Methods 0.000 description 5
- 230000009286 beneficial effect Effects 0.000 description 4
- 230000006870 function Effects 0.000 description 4
- 229910052720 vanadium Inorganic materials 0.000 description 4
- 238000009776 industrial production Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 230000000087 stabilizing effect Effects 0.000 description 3
- 238000003860 storage Methods 0.000 description 3
- 230000008093 supporting effect Effects 0.000 description 3
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 238000004512 die casting Methods 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 239000011777 magnesium Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention belongs to the field of metal material design and preparation, and particularly relates to superfine lamellar dual-phase high-strength and high-toughness low-density steel and a preparation method thereof. Compared with the traditional low-density steel, the ultra-fine lamellar dual-phase high-strength high-toughness low-density steel provided by the invention has the advantages that the weldability of the material can be improved due to the fact that the C content is greatly reduced; mn can regulate and control the austenite stability; the addition of a large amount of Al can not only greatly reduce the density of the steel material, but also improve the corrosion resistance; the addition of Ni can promote the formation of NiAl type B2 phase with certain plastic deformation capability and can also greatly improve corrosion resistance. The invention also provides a preparation method of the superfine lamellar dual-phase high-strength and high-toughness low-density steel, which can obtain the superfine lamellar structure of B2 and austenite in lamellar distribution through simple hot forging, hot rolling or annealing processes, and effectively improves the toughness of the material under the condition of greatly reducing the density.
Description
Technical Field
The invention belongs to the field of metal material design and preparation, and particularly relates to superfine lamellar dual-phase high-strength and high-toughness low-density steel and a preparation method thereof.
Background
The "heavier mass, higher power consumption, and greater energy consumption" is one of the basic attributes of an automobile. The automobile weight reduction is an important technical path for realizing energy conservation and emission reduction of automobiles, and is also a necessary path for sustainable development of automobile industry. At present, structural materials for automobiles mainly comprise steel, magnesium, aluminum, fiber composite materials and the like, wherein the density of the magnesium, aluminum and fiber composite materials is smaller, the realization of light weight is facilitated, but the strength of the materials is low, the price is high, and the materials are greatly limited in practical application. At present, high-strength steel is still favored by domestic and foreign automobile enterprises in terms of high cost performance, driving light and mature application technology, perfect industrial system and good application environment. However, the density and the toughness of the metal material are in an inverted relation, and how to obtain good toughness while reducing the density of the material is a key scientific and technical problem focused in the field.
CN109628850a discloses a multipurpose full austenitic low density steel and a preparation method. The density is 7.0-7.4g/cm 3, the structure type is full austenite+nano-grade VC and MoC precipitated phase, the yield strength of the steel plate can reach more than 1000MPa, the elongation can reach 30%, the area shrinkage can reach 50%, and the V notch low-temperature impact toughness at-40 ℃ can reach 40J/cm 2. However, this method uses carbide as a precipitation strengthening means, resulting in a high yield strength, but the low-temperature impact toughness is not high, and the density is not greatly reduced.
The CN114480988A patent discloses a multiphase composite high-strength high-toughness low-density steel and a preparation method, and the multiphase composite high-strength high-toughness low-density steel with the density less than or equal to 6.6g/cm 3, the yield strength of 585,000 MPa, the tensile strength of 8801100MPa, the elongation of 42 68 percent and the V-shaped notch impact energy of 40 ℃ of more than 50J is obtained through adjustment of alloy components and a processing technology. In this scheme, although the composite phase such as kappa carbide, delta ferrite, niAl phase and NbC precipitation is used for strengthening, the yield strength of the steel is lower and is lower than 1000MPa, and the kappa carbide or NbC precipitation in the low-density steel is easily coarse, so that the low-temperature impact toughness of the steel is deteriorated.
The project provides a new material for the automobile with light weight and high strength and toughness through designing alloy components of steel materials and optimizing processing and heat treatment processes, provides a good material foundation for the light weight design of the automobile, and is beneficial to promoting the low-carbon sustainable development of the automobile industry.
Disclosure of Invention
The invention provides superfine lamellar dual-phase high-strength high-toughness low-density steel and a preparation method thereof, which aim to solve the problems that the yield strength of the existing low-density steel material is too high or too low, and the low-temperature impact toughness is not high.
In order to achieve the above purpose, the invention proposes the following technical scheme:
The superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following chemical components in percentage by mass:
0.4-1.2wt.% of C, 14-35wt.% of Mn, 7-14wt.% of Al, 3-6wt.% of Ni, and the balance of Fe and unavoidable impurities.
Preferably, the chemical components of the ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel further comprise:
V 0-3wt.％、Nb 0-3wt.％、Ti 0-3wt.％、Mo 0-3wt.％。
preferably, in the chemical components of the superfine lamellar dual-phase high-strength high-toughness low-density steel, the content of C is 0.4-0.8wt.%, and the content of Mn is 24-35%.
Preferably, in the chemical components of the superfine lamellar dual-phase high-strength high-toughness low-density steel, the content of C is 0.8-1.2wt.%, and the content of Mn is 14-24%.
Preferably, the structure of the ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel is composed of an ultra-fine lamellar B2 band and austenite.
Preferably, the yield strength of the superfine lamellar dual-phase high-strength high-toughness low-density steel is 800-1500MPa, the tensile strength is 1100-1600MPa, the elongation is 15-50%, the strength-plastic product is 20-50GPa percent, the V notch low-temperature impact toughness at-40 ℃ is 30-70J/cm 2, and the density is 6.1-7.0g/cm 3.
A preparation method of superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following steps:
step 1, preparing materials; fe, mn, C, al, ni with the purity more than or equal to 99.8 percent is weighed according to the chemical component proportion of the superfine lamellar dual-phase high-strength and high-toughness low-density steel to be used as an alloy raw material, and the alloy raw material is put into an electric arc furnace or an induction furnace to be smelted to obtain molten steel;
Step 2, solidifying and casting; injecting the molten steel into a mold for solidification, and casting into an ingot;
step 3, forging; hot forging the cast ingot after cogging, and cooling to room temperature after forging; the forging ratio is more than or equal to 1.5;
Step 4, hot rolling; and carrying out multi-pass hot rolling after forging to obtain a hot rolled sample, and cooling the hot rolled sample to room temperature after annealing to obtain the hot rolled superfine lamellar dual-phase high-strength high-toughness low-density steel.
Preferably, in a specific embodiment, the heat preservation temperature in the step S3 is 1000-1250 ℃, the heat preservation time is 1-6h, and the final heat deformation temperature is more than or equal to 900 ℃.
Preferably, the hot rolling temperature in the step 4 is 600-1200 ℃.
Preferably, the rolling reduction in the step 4 is 80-99%;
the annealing temperature is 500-1000 ℃, and the heat preservation time is 0.05-12h.
The invention has the advantages that:
Compared with the traditional low-density steel, the C content of the ultra-fine lamellar dual-phase high-strength high-toughness low-density steel can be greatly reduced to improve the weldability of the material; the addition of Mn plays a role in stabilizing austenite; the addition of a large amount of Al not only plays a role in reducing the density of steel, but also plays a role in improving the corrosion resistance; the addition of Ni element can promote the formation of NiAl type B2 phase with certain plastic deformation capacity and also can greatly improve corrosion resistance.
The invention also provides a preparation method of the superfine lamellar dual-phase high-strength and high-toughness low-density steel, which can obtain the superfine lamellar structure of B2 and austenite in lamellar distribution through simple hot forging, hot rolling or annealing processes, and can effectively improve the toughness of the material under the condition of greatly reducing the density.
Drawings
The accompanying drawings, which are included to provide a further understanding of the invention and are incorporated in and constitute a part of this specification, illustrate embodiments of the invention and together with the description serve to explain the invention. In the drawings:
FIG. 1 is a schematic flow chart of a preparation method of ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel;
FIG. 2 is an SEM image of a hot rolled ultra-fine lamellar dual-phase high strength and toughness low density steel according to example 1 of the present invention;
FIG. 3 is an SEM image of a hot rolled ultra-fine lamellar dual-phase high strength and toughness low density steel according to example 2 of the present invention;
FIG. 4 is an SEM image of a hot rolled ultra-fine lamellar dual-phase high strength and toughness low density steel according to example 3 of the present invention;
FIG. 5 is an SEM image of a hot rolled ultra-fine lamellar dual-phase high strength and toughness low density steel according to example 4 of the present invention;
FIG. 6 is an SEM image of annealed ultra-fine lamellar dual-phase high-strength low-density steel of example 5 of the invention;
FIG. 7 is an SEM image of annealed ultra-fine lamellar dual-phase high-toughness low-density steel of example 6 of the invention.
Detailed Description
The invention will be described in detail below with reference to the drawings in connection with embodiments. It should be noted that, without conflict, the embodiments of the present invention and features of the embodiments may be combined with each other.
The following detailed description is exemplary and is intended to provide further details of the invention. Unless defined otherwise, all technical terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. The terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of example embodiments in accordance with the invention.
The invention provides superfine lamellar dual-phase high-strength and high-toughness low-density steel, which comprises the following chemical components in percentage by mass: 0.4-1.2wt.% of C, 14-35wt.% of Mn, 7-14wt.% of Al and 3-6wt.% of Ni, and 0-3wt.% of V, 0-3wt.% of Nb, 0-3wt.% of Ti and 0-3wt.% of Mo, and the balance of Fe and unavoidable impurities can be added.
In a specific embodiment, the chemical composition of the ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel can be as follows: 0.4-0.8wt.% of C, 24-35wt.% of Mn, 7-14wt.% of Al and 3-6wt.% of Ni, and 0-3wt.% of V, 0-3wt.% of Nb, 0-3wt.% of Ti and 0-3wt.% of Mo, and the balance of Fe and unavoidable impurities can be added.
In a specific embodiment, the chemical composition of the ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel can be as follows: 0.8-1.2wt.% of C, 14-24wt.% of Mn, 7-14wt.% of Al and 3-6wt.% of Ni, and 0-3wt.% of V, 0-3wt.% of Nb, 0-3wt.% of Ti and 0-3wt.% of Mo, and the balance of Fe and unavoidable impurities can be added.
In a specific embodiment, the structure of the ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel is composed of an ultra-fine lamellar B2 band and austenite.
In a specific embodiment, the ultra-fine lamellar dual-phase high-strength high-toughness low-density steel is characterized in that the yield strength of the ultra-fine lamellar dual-phase high-strength high-toughness low-density steel is 800-1500MPa, the tensile strength is 1100-1600MPa, the elongation is 15-50%, the strength-plastic product is 20-50GPa%, the V notch low-temperature impact toughness at-40 ℃ is 30-70J/cm 2, and the density is 6.1-7.0g/cm 3.
Referring to fig. 1, the invention also provides a preparation method of the ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel, which comprises the following steps of die casting and continuous casting, wherein the die casting is taken as an example:
Step 1, material preparation: fe, mn, C, al, ni with the purity more than or equal to 99.8 percent is weighed according to the chemical component proportion of the superfine lamellar dual-phase high-strength and high-toughness low-density steel to be used as an alloy raw material, V, nb, ti, mo can be added on the basis, and the alloy raw material is placed into an electric arc furnace or an induction furnace for smelting;
step 2, solidification casting: pouring the molten steel obtained in the step 1 into a mould for solidification, and casting into cast ingots;
step 3, forging: cogging the casting blank or the cast ingot obtained in the step 2, performing hot forging, wherein the forging ratio is more than or equal to 1.5, and cooling to room temperature after forging;
Step 4, hot rolling: carrying out multi-pass hot rolling after forging, and then carrying out water quenching, oil quenching or air cooling on a hot rolled sample to room temperature to obtain hot-rolled superfine lamellar dual-phase high-strength low-density steel;
and (3) annealing the sample subjected to hot rolling in the step (4), and then rapidly quenching the sample into water or oil to cool the sample to room temperature to obtain the annealed superfine lamellar dual-phase high-strength high-toughness low-density steel.
In a specific embodiment, the heat preservation temperature in the step S3 is 1000-1250 ℃, the heat preservation time is 1-6h, and the final heat deformation temperature is more than or equal to 900 ℃.
In a specific embodiment, the hot rolling temperature in the step S4 is 600 to 1200 ℃.
In a specific embodiment, the rolling reduction in step S4 is 80-99%.
In one embodiment, the annealing temperature is 500-1000 ℃ and the holding time is 0.05-12h.
Example 1:
The superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following chemical components in percentage by mass: 0.5wt.% of C, 26wt.% of Mn, 11wt.% of Al, 5wt.% of Ni, 0.03wt.% of V, 0.05wt.% of Nb, 0.1wt.% of ti, the balance being Fe and unavoidable impurities.
The preparation method of the superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following steps:
step 1, material preparation: fe, mn, C, al, ni, V, nb, ti, mo with the purity more than or equal to 99.8 percent is weighed according to the chemical component proportion of the superfine lamellar dual-phase high-strength and high-toughness low-density steel and is taken as an alloy raw material, and the alloy raw material is put into an arc melting furnace to be melted under the protection of argon;
step 2, solidification casting: pouring the molten steel obtained in the step 1 into a mould for solidification, and casting into cast ingots;
Step 3, forging: cogging the casting blank or the cast ingot obtained in the step 2, performing hot forging, wherein the forging heat preservation temperature is 1100 ℃, and the heat preservation is carried out for 2 hours, wherein the forging ratio is required to be more than or equal to 1.5, and cooling to room temperature after forging;
Step 4, hot rolling: and (3) preserving heat for 1h at 700 ℃, carrying out multi-pass hot rolling, and then cooling the hot rolled sample to room temperature through water quenching, wherein the total rolling reduction is 98%, so as to obtain the hot rolled superfine lamellar dual-phase high-strength high-toughness low-density steel.
As shown in FIG. 2, the structure of the hot-rolled ultra-fine lamellar dual-phase high-strength and low-density steel is composed of ultra-fine lamellar B2 strips and austenite.
The ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel prepared in the embodiment is subjected to tensile property test, and the tensile property is shown in table 1. The high-strength light-weight steel prepared in example 1 has a yield strength of 1510MPa, a tensile strength of 1591MPa, a total elongation of 22%, a strength-plastic product of 35GPa%, a V notch low-temperature impact toughness of 32J/cm 2 at-40 ℃ and a density of 6.7g/cm 3.
Example 2:
The superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following chemical components in percentage by mass: 0.6wt.% of C, 35wt.% of Mn, 12wt.% of Al, 6wt.% of Ni, 0.05wt.% of V, 0.05wt.% of Nb, the balance being Fe and unavoidable impurities.
The preparation method of the superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following steps:
Step 1, weighing Fe, mn, C, al, ni, V, nb with the purity of more than or equal to 99.8 percent according to the chemical composition ratio of the superfine lamellar dual-phase high-strength and high-toughness low-density steel as an alloy raw material, and putting the alloy raw material into an arc melting furnace for melting under the protection of argon;
step 2, solidification casting: pouring the molten steel obtained in the step 1 into a mould for solidification, and casting into cast ingots;
Step 3, forging: cogging the casting blank or the cast ingot obtained in the step 2, performing hot forging, wherein the forging heat preservation temperature is 1200 ℃, the heat preservation is carried out for 4 hours, the forging ratio is required to be more than or equal to 1.5, and cooling to room temperature after forging;
step 4, hot rolling: and (3) preserving heat for 1h at 800 ℃, carrying out multi-pass hot rolling, and then cooling the hot rolled sample to room temperature through water quenching, wherein the rolling total rolling reduction is 95%, so as to obtain the hot-rolled superfine lamellar dual-phase high-strength high-toughness low-density steel.
As shown in FIG. 3, the structure of the hot-rolled ultra-fine lamellar dual-phase high-strength and low-density steel is composed of ultra-fine lamellar B2 strips and austenite.
The ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel prepared in the embodiment is subjected to tensile property test, and the tensile property is shown in table 1. The high-strength light steel prepared in example 2 has the yield strength of 1373MPa, the tensile strength of 1443MPa, the total elongation of 23%, the strength-plastic product of 33.2GPa percent, the V notch low-temperature impact toughness of minus 40 ℃ of 38J/cm 2 and the density of 6.6g/cm 3.
Example 3:
The superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following chemical components in percentage by mass: 0.9wt.% of C, 20wt.% of Mn, 10wt.% of Al, 4wt.% of Ni, the balance being Fe and unavoidable impurities.
The preparation method of the superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following steps:
step 1, weighing Fe, mn, C, al, ni with the purity of more than or equal to 99.8 percent according to the chemical composition ratio of the superfine lamellar dual-phase high-strength and high-toughness low-density steel as an alloy raw material, and putting the alloy raw material into an arc melting furnace for melting under the protection of argon;
step 2, solidification casting: pouring the molten steel obtained in the step 1 into a mould for solidification, and casting into cast ingots;
Step 3, forging: cogging the casting blank or the cast ingot obtained in the step 2, then carrying out hot forging, wherein the forging heat preservation temperature is 1050 ℃, and the heat preservation is carried out for 3 hours, wherein the forging ratio is more than or equal to 1.5, and cooling to room temperature after forging;
Step 4, hot rolling: and (3) preserving heat for 10min at 1100 ℃, carrying out multi-pass hot rolling, and then cooling the hot rolled sample to room temperature through water quenching, wherein the rolling total rolling reduction is 90%, so as to obtain the hot-rolled superfine lamellar dual-phase high-strength and high-toughness low-density steel.
As shown in FIG. 4, the structure of the hot-rolled ultra-fine lamellar dual-phase high-strength and low-density steel is composed of ultra-fine lamellar B2 bands and austenite.
The ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel prepared in the embodiment is subjected to tensile property test, and the tensile property is shown in table 1. The high-strength light steel prepared in example 3 has a yield strength of 1395MPa, a tensile strength of 1444MPa, a total elongation of 28%, a strength-plastic product of 40.4GPa%, a V notch low-temperature impact toughness of 40J/cm 2 at-40 ℃, and a density of 6.8g/cm 3.
Example 4:
The superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following chemical components in percentage by mass: 0.6wt.% of C, 30wt.% of Mn, 12wt.% of Al, 5wt.% of Ni, 0.15wt.% of V, 0.05wt.% of Nb, 1wt.% of Ti, 1wt.% of Mo, the balance being Fe and unavoidable impurities.
The preparation method of the superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following steps:
Step 1, weighing Fe, mn, C, al, ni, V, nb, ti, mo with the purity of more than or equal to 99.8 percent according to the chemical composition ratio of the superfine lamellar dual-phase high-strength and high-toughness low-density steel as an alloy raw material, and putting the alloy raw material into an arc melting furnace for melting under the protection of argon;
step 2, solidification casting: pouring the molten steel obtained in the step 1 into a mould for solidification, and casting into cast ingots;
step 3, forging: cogging the casting blank or the cast ingot obtained in the step 2, performing hot forging, wherein the forging heat preservation temperature is 1050 ℃, the heat preservation is carried out for 4 hours, the forging ratio is required to be more than or equal to 1.5, and cooling to room temperature after forging;
Step 4, hot rolling: and (3) preserving heat for 1h at 800 ℃, carrying out multi-pass hot rolling, and then cooling the hot rolled sample to room temperature through water quenching, wherein the rolling total rolling reduction is 90%, so as to obtain the hot rolled superfine lamellar dual-phase high-strength high-toughness low-density steel.
As shown in FIG. 5, the microstructure of the hot-rolled ultra-fine lamellar dual-phase high-strength and low-density steel is composed of ultra-fine lamellar B2 strips and austenite.
The ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel prepared in the embodiment is subjected to tensile property test, and the tensile property is shown in table 1. The high-strength light steel prepared in example 4 has a yield strength of 1456MPa, a tensile strength of 1500MPa, a total elongation of 15.4%, a strength-plastic product of 23.1GPa%, a V notch low-temperature impact toughness of 30J/cm 2 at-40 ℃ and a density of 6.4g/cm 3.
Example 5:
The superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following chemical components in percentage by mass: 1.0wt.% of C, 18wt.% of Mn, 10wt.% of Al, 5wt.% of Ni, 0.03wt.% of Nb, the balance being Fe and unavoidable impurities.
The preparation method of the superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following steps:
Step 1, weighing Fe, mn, C, al, ni, nb with the purity of more than or equal to 99.8 percent according to the chemical composition ratio of the superfine lamellar dual-phase high-strength and high-toughness low-density steel as an alloy raw material, and putting the alloy raw material into an arc melting furnace for melting under the protection of argon;
step 2, solidification casting: pouring the molten steel obtained in the step 1 into a mould for solidification, and casting into cast ingots;
Step 3, forging: cogging the casting blank or the cast ingot obtained in the step 2, then carrying out hot forging, wherein the forging heat preservation temperature is 1050 ℃, and the heat preservation is carried out for 1h, wherein the forging ratio is more than or equal to 1.5, and cooling to room temperature after forging;
Step 4, hot rolling: and (3) preserving heat for 1h at 700 ℃, carrying out multi-pass hot rolling, and then cooling the hot rolled sample to room temperature through water quenching, wherein the rolling total rolling reduction is 95%, so as to obtain the hot-rolled superfine lamellar dual-phase high-strength high-toughness low-density steel.
And further, annealing the sample subjected to hot rolling in the step 4, wherein the annealing temperature is 800 ℃, the annealing time is 30min, and then rapidly quenching the sample into water and cooling the sample to room temperature to obtain the annealed superfine lamellar dual-phase high-strength and high-toughness low-density steel.
As shown in FIG. 6, the microstructure of the hot-rolled ultra-fine lamellar dual-phase high-strength and low-density steel is composed of ultra-fine lamellar B2 strips and austenite.
The ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel prepared in the embodiment is subjected to tensile property test, and the tensile property is shown in table 1. The high-strength light-weight steel prepared in the example 1 has the yield strength of 1088MPa, the tensile strength of 1296MPa, the total elongation of 42.4%, the strength-plastic product of 55GPa percent, the V notch low-temperature impact toughness of minus 40 ℃ of 60J/cm 2 and the density of 6.7g/cm 3.
Example 6:
The superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following chemical components in percentage by mass: 0.5wt.% of C, 26wt.% of Mn, 11wt.% of Al, 5wt.% of Ni, the balance being Fe and unavoidable impurities.
The preparation method of the superfine lamellar dual-phase high-strength and high-toughness low-density steel comprises the following steps:
step 1, weighing Fe, mn, C, al, ni with the purity of more than or equal to 99.8 percent according to the chemical composition ratio of the superfine lamellar dual-phase high-strength and high-toughness low-density steel as an alloy raw material, and putting the alloy raw material into an arc melting furnace for melting under the protection of argon;
step 2, solidification casting: pouring the molten steel obtained in the step 1 into a mould for solidification, and casting into cast ingots;
Step 3, forging: cogging the casting blank or the cast ingot obtained in the step 2, then carrying out hot forging, wherein the forging heat preservation temperature is 1100 ℃, and the heat preservation is carried out for 1h, wherein the forging ratio is required to be more than or equal to 1.5, and cooling to room temperature after forging;
Step 4, hot rolling: and (3) preserving heat for 1h at 700 ℃, carrying out multi-pass hot rolling, and then cooling the hot rolled sample to room temperature through water quenching, wherein the total rolling reduction is 98%, so as to obtain the hot rolled superfine lamellar dual-phase high-strength high-toughness low-density steel.
And further, annealing the sample subjected to hot rolling in the step 4, wherein the annealing temperature is 800 ℃, the annealing time is 15min, and then rapidly quenching the sample into water and cooling the sample to room temperature to obtain the annealed superfine lamellar dual-phase high-strength and high-toughness low-density steel.
As shown in FIG. 7, the microstructure of the hot-rolled ultra-fine lamellar dual-phase high-strength low-density steel is composed of ultra-fine lamellar B2 strips and austenite.
The ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel prepared in the embodiment is subjected to tensile property test, and the tensile property is shown in table 1. The high-strength light-weight steel prepared in example 6 has the yield strength of 1058MPa, the tensile strength of 1286MPa, the total elongation of 43%, the strength-plastic product of 55GPa percent, the V notch low-temperature impact toughness of minus 40 ℃ of 63J/cm 2 and the density of 6.8g/cm 3.
Table 1 mechanical property data of ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel are obtained in each example
In the scheme, compared with the high-strength low-density steel in the prior art:
compared with the traditional low-density steel, the C content can be greatly reduced in terms of components so as to improve the weldability of the material; the addition of Mn plays a role in stabilizing austenite; the addition of a large amount of Al not only plays a role in reducing the density of steel, but also plays a role in improving the corrosion resistance; the addition of Ni element can promote the formation of NiAl type B2 phase with certain plastic deformation capacity and also can greatly improve corrosion resistance. From the aspect of the hot working process, the superfine wafer layer structure with B2 and austenite distributed in a layered manner can be prepared by a simple hot forging, hot rolling or annealing process, and the toughness of the material can be effectively improved under the condition of greatly reducing the density.
The yield strength of the superfine lamellar dual-phase high-strength high-toughness low-density steel is 800-1500MPa, the tensile strength is 1100-1600MPa, the elongation is 15-50%, the strength-plastic product is 20-50GPa percent, the V notch low-temperature impact toughness at-40 ℃ is 30-70J/cm 2, the density is 6.1-7.0g/cm 3, and the requirements of new materials for light-weight high-strength high-toughness automobiles are met.
The preparation process of the finished steel product is simple and economical, and can realize large-scale industrial production. The development of the superfine lamellar dual-phase high-strength and high-toughness low-density steel provides a good material foundation for the light design of automobiles, is beneficial to pushing the low-carbon sustainable development of the automobile industry, and has an important supporting effect on the development of the intelligent automobile key part industry and the advanced layout of related technologies in China.
In the scheme, compared with the high-strength low-density steel in the prior art: compared with the traditional low-density steel, the finished steel product has greatly reduced C content, and can improve the weldability of the material; mn can stabilize austenite; the addition of a large amount of Al can not only greatly reduce the density of the steel material, but also improve the corrosion resistance; the addition of Ni can promote the formation of NiAl type B2 phase with certain plastic deformation capability and can also greatly improve corrosion resistance. From the aspect of the hot working process, the superfine wafer layer structure with B2 and austenite distributed in a layered manner can be obtained through simple hot forging, hot rolling or annealing process, and the toughness of the material can be effectively improved under the condition of greatly reducing the density.
The yield strength of the superfine lamellar dual-phase high-strength high-toughness low-density steel is 800-1500MPa, the tensile strength is 1100-1600MPa, the elongation is 15-50%, the strength-plastic product is 20-50GPa percent, the V notch low-temperature impact toughness at-40 ℃ is 30-70J/cm 2, the density is 6.1-7.0g/cm 3, and the requirements of new materials for light-weight high-strength high-toughness automobiles are met.
The preparation process of the finished steel product is simple and economical, and can realize large-scale industrial production. The development of the superfine lamellar dual-phase high-strength and high-toughness low-density steel provides a good material foundation for the light design of automobiles, is beneficial to pushing the low-carbon sustainable development of the automobile industry, and has an important supporting effect on the development of the intelligent automobile key part industry and the advanced layout of related technologies in China.
In the scheme, compared with the high-strength low-density steel in the prior art: compared with the traditional low-density steel, the C content can be greatly reduced in terms of components so as to improve the weldability of the material; the addition of Mn plays a role in stabilizing austenite; the addition of a large amount of Al not only plays a role in reducing the density of steel, but also plays a role in improving the corrosion resistance; the addition of Ni element can promote the formation of NiAl type B2 phase with certain plastic deformation capacity and also can greatly improve corrosion resistance. From the aspect of the hot working process, the superfine wafer layer structure with B2 and austenite distributed in a layered manner can be obtained through simple hot forging, hot rolling or annealing process, and the toughness of the material can be effectively improved under the condition of greatly reducing the density.
The yield strength of the superfine lamellar dual-phase high-strength high-toughness low-density steel is 800-1500MPa, the tensile strength is 1100-1600MPa, the elongation is 15-50%, the strength-plastic product is 20-50GPa percent, the V notch low-temperature impact toughness at-40 ℃ is 30-70J/cm 2, the density is 6.1-7.0g/cm 3, and the requirements of new materials for light-weight high-strength high-toughness automobiles are met.
The preparation process of the finished steel product is simple and economical, and can realize large-scale industrial production. The development of the superfine lamellar dual-phase high-strength and high-toughness low-density steel provides a good material foundation for the light design of automobiles, is beneficial to pushing the low-carbon sustainable development of the automobile industry, and has an important supporting effect on the development of the intelligent automobile key part industry and the advanced layout of related technologies in China.
It will be appreciated by those skilled in the art that the present invention can be carried out in other embodiments without departing from the spirit or essential characteristics thereof. Accordingly, the above disclosed embodiments are illustrative in all respects, and not exclusive. All changes that come within the scope of the invention or equivalents thereto are intended to be embraced therein.
It will be appreciated by those skilled in the art that embodiments of the present invention may be provided as a method, system, or computer program product. Accordingly, the present invention may take the form of an entirely hardware embodiment, an entirely software embodiment or an embodiment combining software and hardware aspects. Furthermore, the present invention may take the form of a computer program product embodied on one or more computer-usable storage media (including, but not limited to, disk storage, CD-ROM, optical storage, and the like) having computer-usable program code embodied therein.
The present invention is described with reference to flowchart illustrations and/or block diagrams of methods, apparatus (systems) and computer program products according to embodiments of the invention. It will be understood that each flow and/or block of the flowchart illustrations and/or block diagrams, and combinations of flows and/or blocks in the flowchart illustrations and/or block diagrams, can be implemented by computer program instructions. These computer program instructions may be provided to a processor of a general purpose computer, special purpose computer, embedded processor, or other programmable data processing apparatus to produce a machine, such that the instructions, which execute via the processor of the computer or other programmable data processing apparatus, create means for implementing the functions specified in the flowchart flow or flows and/or block diagram block or blocks.
These computer program instructions may also be stored in a computer-readable memory that can direct a computer or other programmable data processing apparatus to function in a particular manner, such that the instructions stored in the computer-readable memory produce an article of manufacture including instruction means which implement the function specified in the flowchart flow or flows and/or block diagram block or blocks.
These computer program instructions may also be loaded onto a computer or other programmable data processing apparatus to cause a series of operational steps to be performed on the computer or other programmable apparatus to produce a computer implemented process such that the instructions which execute on the computer or other programmable apparatus provide steps for implementing the functions specified in the flowchart flow or flows and/or block diagram block or blocks.
Finally, it should be noted that: the above embodiments are only for illustrating the technical aspects of the present invention and not for limiting the same, and although the present invention has been described in detail with reference to the above embodiments, it should be understood by those of ordinary skill in the art that: modifications and equivalents may be made to the specific embodiments of the invention without departing from the spirit and scope of the invention, which is intended to be covered by the claims.
Claims (10)
1. The superfine lamellar dual-phase high-strength and high-toughness low-density steel is characterized by comprising the following chemical components in percentage by mass:
0.4-1.2wt.% of C, 14-35wt.% of Mn, 7-14wt.% of Al, 3-6wt.% of Ni, and the balance of Fe and unavoidable impurities.
2. The ultra-fine lamellar dual phase high strength and toughness low density steel in accordance with claim 1, characterized in that the chemical composition of the ultra-fine lamellar dual phase high strength and toughness low density steel further comprises:
V 0-3wt.％、Nb 0-3wt.％、Ti 0-3wt.％、Mo 0-3wt.％。
3. The ultra-fine lamellar dual-phase high-strength and low-density steel according to claim 1, characterized in that the chemical composition of the ultra-fine lamellar dual-phase high-strength and low-density steel is 0.4-0.8wt.% C and 24-35% Mn.
4. The ultra-fine lamellar dual-phase high-strength and low-density steel according to claim 1, characterized in that the chemical composition of the ultra-fine lamellar dual-phase high-strength and low-density steel is 0.8-1.2wt.% C and 14-24% Mn.
5. The ultra-fine lamellar dual phase high strength and toughness low density steel according to claim 1, characterized in that the structure of the ultra-fine lamellar dual phase high strength and toughness low density steel is composed of ultra-fine lamellar B2 bands and austenite.
6. The ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel according to claim 1, characterized in that the yield strength of the ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel is 800-1500MPa, the tensile strength is 1100-1600MPa, the elongation is 15-50%, the product of strength and elongation is 20-50gpa%, the V notch low-temperature impact toughness at-40 ℃ is 30-70J/cm 2, and the density is 6.1-7.0g/cm 3.
7. A method for preparing the ultra-fine lamellar dual-phase high-toughness low-density steel according to any one of claims 1 to 6, which is characterized by comprising the following steps:
step 1, preparing materials; fe, mn, C, al, ni with the purity more than or equal to 99.8 percent is weighed according to the chemical component proportion of the superfine lamellar dual-phase high-strength and high-toughness low-density steel to be used as an alloy raw material, and the alloy raw material is put into an electric arc furnace or an induction furnace to be smelted to obtain molten steel;
Step 2, solidifying and casting; injecting the molten steel into a mold for solidification, and casting into an ingot;
step 3, forging; hot forging the cast ingot after cogging, and cooling to room temperature after forging; the forging ratio is more than or equal to 1.5;
Step 4, hot rolling; and carrying out multi-pass hot rolling after forging to obtain a hot rolled sample, and cooling the hot rolled sample to room temperature after annealing to obtain the hot rolled superfine lamellar dual-phase high-strength high-toughness low-density steel.
8. The method of claim 7, wherein in one embodiment, the heat preservation temperature in the step S3 is 1000-1250 ℃, the heat preservation time is 1-6h, and the final heat distortion temperature is not less than 900 ℃.
9. The method for producing ultra-fine lamellar dual-phase high strength and toughness low density steel according to claim 7, characterized in that the hot rolling temperature in the step 4 is 600-1200 ℃.
10. The method for preparing ultra-fine lamellar dual-phase high-strength and high-toughness low-density steel according to claim 7, wherein the rolling reduction in the step 4 is 80-99%;
the annealing temperature is 500-1000 ℃, and the heat preservation time is 0.05-12h.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202311808667.XA CN117904543A (en) | 2023-12-26 | 2023-12-26 | Superfine lamellar dual-phase high-strength and high-toughness low-density steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202311808667.XA CN117904543A (en) | 2023-12-26 | 2023-12-26 | Superfine lamellar dual-phase high-strength and high-toughness low-density steel and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN117904543A true CN117904543A (en) | 2024-04-19 |
Family
ID=90680949
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202311808667.XA Pending CN117904543A (en) | 2023-12-26 | 2023-12-26 | Superfine lamellar dual-phase high-strength and high-toughness low-density steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN117904543A (en) |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20180100220A1 (en) * | 2016-10-12 | 2018-04-12 | Hyundai Motor Company | High Manganese Steel |
| CN108018494A (en) * | 2017-11-30 | 2018-05-11 | 安徽工业大学工商学院 | A kind of production method for the annealing process and low density steel for improving the strong plasticity of low density steel |
| CN113278896A (en) * | 2021-01-12 | 2021-08-20 | 北京科技大学 | Fe-Mn-Al-C series high-strength low-density steel and preparation method thereof |
| CN115572885A (en) * | 2022-09-09 | 2023-01-06 | 钢铁研究总院有限公司 | Manufacturing method of high-strength high-toughness plastic austenite type low-density steel |
| CN116288021A (en) * | 2023-02-06 | 2023-06-23 | 武汉科技大学 | High-strength and high-toughness dual-phase low-density steel and preparation method and application thereof |
-
2023
- 2023-12-26 CN CN202311808667.XA patent/CN117904543A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20180100220A1 (en) * | 2016-10-12 | 2018-04-12 | Hyundai Motor Company | High Manganese Steel |
| CN108018494A (en) * | 2017-11-30 | 2018-05-11 | 安徽工业大学工商学院 | A kind of production method for the annealing process and low density steel for improving the strong plasticity of low density steel |
| CN113278896A (en) * | 2021-01-12 | 2021-08-20 | 北京科技大学 | Fe-Mn-Al-C series high-strength low-density steel and preparation method thereof |
| CN115572885A (en) * | 2022-09-09 | 2023-01-06 | 钢铁研究总院有限公司 | Manufacturing method of high-strength high-toughness plastic austenite type low-density steel |
| CN116288021A (en) * | 2023-02-06 | 2023-06-23 | 武汉科技大学 | High-strength and high-toughness dual-phase low-density steel and preparation method and application thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN113278896B (en) | Fe-Mn-Al-C series high-strength low-density steel and preparation method thereof | |
| CN105624550B (en) | Nuclear island equipment big thickness SA738GrB steel plates and production method | |
| CN103556020B (en) | There is the high Mn content high-damping mn-cu-based alloy of excellent mechanical property | |
| CN102703811B (en) | Titanium micro-alloyed 400MPa grade high-strength steel bar and production method thereof | |
| CN102181805B (en) | Steel plate and method thereof used for producing water heater linear enamel by flexible thin slab rolling line | |
| CN108796363B (en) | High-surface-quality aluminum-coated substrate steel suitable for large deformation and stamping and production method thereof | |
| CN108220766B (en) | Cr-V hot work die steel and preparation method thereof | |
| CN110230009B (en) | Hot work die steel with good cutting performance and preparation method thereof | |
| CN103255349A (en) | Small-size 600MPa-level aseimatic twisted steel and manufacturing method thereof | |
| CN103725986A (en) | High-ductility Class F extra thick rack steel plate used at low temperature and manufacturing method of steel plate | |
| CN110284042B (en) | Superplastic high-entropy alloy, sheet and preparation method thereof | |
| CN110541124B (en) | Nitrogenous plastic die steel slab and process method thereof | |
| CN112222572A (en) | Gas shielded welding wire steel and production method thereof | |
| CN104120368A (en) | High-strength austenitic stainless steel for automobile frames and manufacturing method thereof | |
| CN102634738A (en) | Supporting roller with roughness keeping capability and manufacturing method thereof | |
| CN102181794A (en) | Hardening and tempering high-strength steel plate for wood based panel equipment and production method of tempering high-strength steel plate | |
| CN103540850A (en) | Super-thick steel with yield strength >= 550MPa for engineering machinery as well as production method thereof | |
| CN102851596A (en) | Fire resistant steel plate for 490 MPa grade building structure with low cost and manufacture method thereof | |
| CN105603303B (en) | A kind of high strength ultra-thick steel plates | |
| CN103469069B (en) | Austenite low-permeability steel with lower yield strength not less than 810MPa and production method | |
| CN102634727B (en) | High-toughness steel for engineering machine and production method thereof by using TMCP (Thermal Mechanical Control Processing) | |
| CN117904543A (en) | Superfine lamellar dual-phase high-strength and high-toughness low-density steel and preparation method thereof | |
| CN102181792B (en) | Low-cost high-strength high-toughness shock-proof refractory steel and preparation technique thereof | |
| CN110218935B (en) | Hot-work die steel with three-dimensional isotropic performance and preparation method thereof | |
| CN104862572A (en) | High-strength high-ductility high-alloy steel and manufacturing method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination |