CN110714167A - Austenitic alloy steel and manufacturing method thereof - Google Patents
Austenitic alloy steel and manufacturing method thereof Download PDFInfo
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- CN110714167A CN110714167A CN201810932982.6A CN201810932982A CN110714167A CN 110714167 A CN110714167 A CN 110714167A CN 201810932982 A CN201810932982 A CN 201810932982A CN 110714167 A CN110714167 A CN 110714167A
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- 229910000851 Alloy steel Inorganic materials 0.000 title claims abstract description 114
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 24
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 29
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 28
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 23
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 23
- 239000011733 molybdenum Substances 0.000 claims abstract description 23
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 18
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 17
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 17
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 10
- 229910052742 iron Inorganic materials 0.000 claims abstract description 10
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims abstract description 8
- 230000032683 aging Effects 0.000 claims description 28
- 229910045601 alloy Inorganic materials 0.000 claims description 27
- 239000000956 alloy Substances 0.000 claims description 27
- 238000010791 quenching Methods 0.000 claims description 15
- 230000000171 quenching effect Effects 0.000 claims description 15
- 238000005266 casting Methods 0.000 claims description 13
- 229910052748 manganese Inorganic materials 0.000 claims description 13
- 239000011572 manganese Substances 0.000 claims description 13
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 13
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 11
- 238000000034 method Methods 0.000 claims description 11
- 239000000203 mixture Substances 0.000 claims description 11
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 9
- 229910052804 chromium Inorganic materials 0.000 claims description 9
- 239000011651 chromium Substances 0.000 claims description 9
- 239000010941 cobalt Substances 0.000 claims description 6
- 229910017052 cobalt Inorganic materials 0.000 claims description 6
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 6
- 238000002844 melting Methods 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- 239000004411 aluminium Substances 0.000 claims 1
- 229910000831 Steel Inorganic materials 0.000 abstract description 33
- 239000010959 steel Substances 0.000 abstract description 33
- 238000012360 testing method Methods 0.000 description 21
- 238000010438 heat treatment Methods 0.000 description 15
- 229910001339 C alloy Inorganic materials 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 12
- 238000000879 optical micrograph Methods 0.000 description 11
- 150000001247 metal acetylides Chemical class 0.000 description 10
- 239000000463 material Substances 0.000 description 8
- 230000008569 process Effects 0.000 description 6
- -1 iron-manganese-aluminum-carbon Chemical compound 0.000 description 5
- 238000003723 Smelting Methods 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 3
- 229910002059 quaternary alloy Inorganic materials 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 229910000616 Ferromanganese Inorganic materials 0.000 description 2
- RQMIWLMVTCKXAQ-UHFFFAOYSA-N [AlH3].[C] Chemical compound [AlH3].[C] RQMIWLMVTCKXAQ-UHFFFAOYSA-N 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000010955 niobium Substances 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000001330 spinodal decomposition reaction Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 239000010937 tungsten Substances 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 238000007550 Rockwell hardness test Methods 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 239000012943 hotmelt Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000002105 nanoparticle Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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- C21D1/34—Methods of heating
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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- C21D6/00—Heat treatment of ferrous alloys
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
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Abstract
The present invention provides an austenitic (Austenite) alloy steel comprising 25 to 31 wt.% manganese, 7 to 10 wt.% aluminum, 1.2 to 1.6 wt.% carbon, less than 6 wt.% molybdenum, and the balance iron. The austenitic alloy steel has high strength, high ductility and high-temperature strength, and the density is 6.6-6.8g/cm3And is 14 percent lighter than the traditional die steel. In addition, the invention also provides a manufacturing method of the austenitic alloy steel.
Description
Technical Field
The present invention relates to an austenitic alloy steel, and more particularly, to an austenitic alloy steel suitable for use in manufacturing hot-working tools.
Background
The martensite steel material has excellent mechanical properties such as hardness and toughness, and is therefore often used as a material for forming hot-working tools, however, the martensite steel material has poor ductility, and may cause cracking of the formed hot-working tools.
AISI H13 steel is one of the martensite steels used to make hot work tools, comprising 0.32 to 0.45 wt.% carbon, 0.8 to 1.2 wt.% silicon, 0.20 to 0.50 wt.% manganese, 4.75 to 5.5 wt.% chromium, 1.10 to 1.75 wt.% molybdenum, 0.8 to 1.2 wt.% vanadium, not more than 0.03 wt.% phosphorus, not more than 0.03 wt.% sulfur, and the balance iron. Said AISI H13 steel has a Rockwell hardness at room temperature of up to 55 to 58, an elongation of 3 to 5%, and is generally used to reduce the Rockwell hardness of said AISI H13 steel to 42 to 50, increase the elongation to 5 to 8%, an impact toughness of 5 to 10 joules, and a Rockwell C hardness at high temperature (HRc) of 33 to 41, because of the low elongation which is brittle in use.
QRO 90 steel is another martensite steel used to make hot-work tools, and comprises 0.38 wt.% carbon, 0.30 wt.% silicon, 0.75 wt.% manganese, 2.60 wt.% chromium, 2.25 wt.% molybdenum, 0.9 wt.% vanadium, and the balance iron. The QRO 90 steel has a room temperature Rockwell hardness of 45, an elongation of 11%, an impact toughness of 10 joules, and a high temperature Rockwell C hardness (HRc) of 26 to 41.
On the other hand, iron-manganese-aluminum-carbon austenitic (Austenite) steels have been extensively studied over the past decades because of their potential applications due to their high mechanical strength and high ductility characteristics.
Generally, when the carbon content of the steel alloy exceeds about 1.2 wt.%, the ductility of the alloy will be severely deteriorated or called embrittling. Therefore, in the prior art of studying austenitic alloy systems, the amount of carbon in the alloy is controlled to be between 0.54 and 1.3 wt.%. However, although the addition of the above elements can increase the mechanical strength of the fe-mn-al-c austenitic steel material, the problem of ductility (i.e., elongation) reduction is also caused because the alloy is easy to precipitate coarse carbides at austenite grain boundaries during aging treatment, so that hot working tools made of the steel material are easy to crack during use.
Applicant's united states patent No. 9,528,177 discloses a fe-mn-al-c quaternary alloy having specific contents of iron, manganese, aluminum, and carbon, which can form high-density and fine k' -carbides in an austenite-based phase by spinodal decomposition (spinodal decomposition) phase transformation mechanism during quenching after Solutionizing (SHT) by controlling the carbon content to be between 1.4 wt.% and 2.2 wt.%, resulting in excellent ductility and high mechanical strength. However, the addition of strong carbide-forming elements, such as chromium, titanium, and molybdenum, to the fe-mn-al-c quaternary alloy does not have a significant effect on the formation of high density and fine κ' -carbides in the austenite-based phase, and thus the addition of the strong carbide-forming elements to the fe-mn-al-c quaternary alloy is not suggested.
Disclosure of Invention
The object of the present invention is to provide an austenitic (Austenite) alloy steel having excellent mechanical properties at room temperature without affecting ductility and having excellent strength even at high temperatures.
The austenitic alloy steel of the present invention comprises 25 to 31 wt.% manganese, 7 to 10 wt.% aluminum, 1.2 to 1.6 wt.% carbon, greater than 0 to less than 6 wt.% molybdenum, and the balance iron.
Preferably, the austenitic alloy steel, wherein the proportion of manganese is between 26 and 30 wt.%, and the proportion of aluminum is between 8 and 10 wt.%.
Preferably, the austenitic alloy steel, wherein the proportion of manganese is between 27 and 29 wt.%, and the proportion of molybdenum is between 2 and 6 wt.%.
Preferably, the austenitic alloy steel, wherein the proportion of aluminum is between 8 wt.% and 9 wt.%.
Preferably, the austenitic alloy steel, wherein the proportion of carbon is 1.4 wt.% to 1.6 wt.%.
Preferably, the austenitic alloy steel, wherein the proportion of molybdenum is between 2 wt.% and 6 wt.%.
Preferably, the austenitic alloy steel further comprises chromium in a proportion of less than 6 wt.%.
Preferably, the austenitic alloy steel further comprises cobalt in a proportion of less than 5 wt.%.
Preferably, the austenitic alloy steel is a full austenitic phase, and has an elongation of 20 to 40% at 25 ℃, an ultimate tensile strength of greater than 1250MPa, and an ultimate tensile strength of greater than 1000MPa at 300 ℃.
Another object of the present invention is to provide a method for manufacturing the austenitic alloy steel, including: step (a): melting the alloy composition into a casting; step (b): performing hot working treatment on the casting at 1100-950 ℃ to form a hot-working piece; step (c): carrying out primary water quenching on the hot work piece after the hot work treatment; and step (d): and (3) carrying out aging treatment on the hot work piece subjected to the first water quenching at 480-600 ℃.
Preferably, in the manufacturing method of the austenitic alloy steel, the aging treatment time is 5 to 12 hours when the temperature of the aging treatment is 480 ℃ to 500 ℃, and the aging treatment time is 1 to 4 hours when the temperature of the aging treatment is more than 500 ℃ to 600 ℃.
Preferably, the manufacturing method of the austenitic alloy steel further comprises a step (e) of performing secondary water quenching on the aged hot work piece.
Preferably, the method of manufacturing an austenitic alloy steel includes the step (b) of subjecting the casting to a hot working treatment to a thickness of at least less than 25% of the thickness of the casting.
Preferably, the austenitic alloy steel prepared by the manufacturing method has the elongation of 20-40% at room temperature and the ultimate tensile strength of more than 1000MPa at 300 ℃.
Preferably, the yield strength of the austenitic alloy steel prepared by the manufacturing method is 1230-1350 MPa and the ultimate tensile strength is 1280-1386 MPa at room temperature.
Preferably, the austenitic alloy steel prepared by the manufacturing method has Rockwell hardness of 45-48 at room temperature.
Preferably, the yield strength of the austenitic alloy steel prepared by the manufacturing method is more than 970MPa at 300 ℃.
Preferably, the yield strength of the austenitic alloy steel prepared by the manufacturing method is more than 650MPa and the ultimate tensile strength is more than 700MPa at 500 ℃.
Preferably, the austenitic alloy steel prepared by the manufacturing method has yield strength of 410-420 MPa and ultimate tensile strength of 440-449 MPa at 700 ℃.
The invention has the following effects: by adding less than 6 wt.% of molybdenum to a special composition of Fe-Al-Mn-C austenitic alloy steel, the austenitic alloy steel has excellent mechanical properties at room temperature, and ultimate tensile strength, and also has good strength performance at high temperature (500 ℃).
Drawings
FIG. 1 is a block diagram of a process for making an austenitic (Austenitic) alloy steel according to the present invention;
FIG. 2 is an optical micrograph of an austenitic alloy steel according to example 1 of the present invention after heat treatment;
FIG. 3 is an optical micrograph of an austenitic alloy steel according to example 3 of the present invention after heat treatment;
FIG. 4 is an optical micrograph of an austenitic alloy steel according to an embodiment 8 of the present invention after heat treatment;
FIG. 5 is an optical micrograph of a specific example 1 of the austenitic alloy steel of the present invention after aging treatment;
FIG. 6 is an optical micrograph of an aged austenitic alloy steel of example 3 according to the present invention;
FIG. 7 is an optical micrograph of an aged austenitic alloy steel according to example 8 of the present invention;
FIG. 8 is an optical micrograph of an austenitic alloy steel according to the present invention of comparative example 1 after heat treatment; and
FIG. 9 is an optical micrograph of an austenitic alloy steel according to the present invention after heat treatment in comparative example 2.
Detailed Description
The present invention discloses an austenitic (Austenite) alloy steel having high strength and high ductility, which can be applied to general steel plates such as automobile steel plates, parts such as gears, or hot die steel, and a method for manufacturing the same.
The alloy composition of the austenitic alloy steel comprises 25 to 31 wt.% manganese, 7 to 10 wt.% aluminum, 1.2 to 1.6 wt.% carbon, greater than 0 to less than 6 wt.% molybdenum, and the balance iron.
Manganese is an austenite strengthening element, and has better ductility compared to a body-centered-cubic (BCC) structure or a hexagonal close-packed (HCP) structure since the austenite phase has a face-centered-cubic (FCC) structure and more slip systems. In order to obtain a complete austenitic structure at room temperature, the manganese content in the austenitic steel alloy according to the invention is therefore 25 wt.% to 31 wt.%. In some embodiments, the manganese content of the austenitic alloy steel is between 26 wt.% and 30 wt.%. In some embodiments, the manganese content of the austenitic alloy steel is between 27 wt.% and 29 wt.%.
Aluminum is formed (Fe, Mn)3AlCxThe main elements of the carbides (i.e., kappa' -carbides) in the present inventionThe aluminum content in the matrix alloy steel is 7 wt.% to 10 wt.%. In some embodiments, the aluminum content of the austenitic alloy steel is between 8 wt.% and 10 wt.%. In some embodiments, the aluminum content of the austenitic alloy steel is between 8 wt.% and 9 wt.%.
The carbon content in the austenitic alloy steels according to the invention is between 1.2 wt.% and 1.6 wt.%, higher than the carbon content of known ferro-manganese-aluminum-carbon austenitic steels containing molybdenum, niobium, and/or tungsten (i.e. up to 1.0 wt.%). In some embodiments, the carbon content of the austenitic alloy steel is 1.3 wt.% to 1.6 wt.%. In some embodiments, the carbon content of the austenitic alloy steel is 1.4 wt.% to 1.6 wt.%.
Molybdenum is a strong carbide former and is present in the austenitic alloy steels of the present invention in an amount greater than 0 wt.% and less than 6 wt.%. In some embodiments, the molybdenum content of the austenitic alloy steel is between 2 wt.% and 6 wt.%.
In some embodiments, the austenitic alloy steel further comprises chromium, also a strong carbide forming element, and the content of chromium is less than 6 wt.%.
In some embodiments, the austenitic alloy steel further comprises cobalt, also a strong carbide former, and the content of cobalt is less than 5 wt.%.
It should be noted that the content of low melting point elements (such as manganese and aluminum) in the austenitic alloy steel may cause the actual content of some elements in the austenitic alloy steel produced by volatilization during smelting to be different from the addition amount during smelting, however, the difference between the two is not large, and the properties of the austenitic alloy steel finally produced are not affected within the allowable error range.
Referring to fig. 1, the method for manufacturing the austenitic alloy steel includes steps 91 to 95.
And step 91, smelting the alloy composition of the austenitic alloy steel into a casting in a high-frequency smelting furnace under the atmosphere.
Then, step 92 is performed to heat treat (e.g., hot rolling, hot forging, etc.) the casting to a predetermined shape at 1100 ℃ to 950 ℃ to form a hot worked article.
Then, in step 93, the hot work piece is subjected to a first water quenching and cooled to room temperature.
In detail, when the temperature of the Aging treatment is between 480 ℃ and 500 ℃, the time (Aging time) of the Aging treatment is 5 to 12 hours; when the temperature of the aging treatment is more than 500 ℃, the time of the aging treatment is 1 to 4 hours.
And finally, step 95, performing secondary water quenching on the hot-worked piece subjected to the aging treatment, and cooling to room temperature to finish the manufacturing of the austenitic alloy steel.
The manufacturing process of the austenitic alloy steel is different from the prior ferro-manganese-aluminum-carbon alloy steel which has lower carbon content and contains strong carbide forming elements, after the prior ferro-manganese-aluminum-carbon alloy steel which has low carbon content and contains strong carbide forming elements is hot-processed, solid solution heat treatment is needed, coarse carbides precipitated on a grain boundary are re-dissolved in a base phase to improve the ductility of the iron-manganese-aluminum-carbon alloy steel, the austenitic alloy steel of the present invention has a high content of carbon and strong carbide-forming elements, however, the present invention utilizes control of the temperature of the hot working treatment (hot rolling or hot forging) (1100 ℃ to 950 ℃), therefore, the composition of the iron-manganese-aluminum-carbon alloy can be prevented from separating out coarse carbides on grain boundaries in the hot working process, and the austenitic alloy steel prepared can have both strength and ductility without a solution heat treatment step after the hot working process.
It should be noted that the step 95 may not be performed according to the manufacturing process, and the hot working piece may be naturally cooled to room temperature after aging treatment without performing a second water quenching. Furthermore, the present invention utilizes the control of the hot working temperature to effectively avoid the precipitation of coarse carbides to affect the ductility of the alloy steel, thereby eliminating the need for conventional hot-melt processes and effectively reducing the overall process time. However, the hot working treatment and the first water quenching may be optionally followed by a hot melting step, which does not affect the overall properties of the alloy steel.
Particularly, the austenitic alloy steel prepared by the austenitic alloy composition and the manufacturing method of the invention is a complete austenitic phase, the Yield Strength (YS) at room temperature (25 ℃) is between 1200MPa and 1400MPa, the Rockwell C hardness (HRc) is between 45 and 55, the ultimate tensile strength is between 1200MPa and 1500MPa, and the elongation (El) is between 20 percent and 40 percent, and meanwhile, the austenitic alloy steel has good Yield Strength (YS) and Ultimate Tensile Strength (UTS) at high temperature (less than 700 ℃). Therefore, the austenitic alloy steel can be used as a common steel plate (such as an automobile steel plate) and a part (such as a gear), and is more suitable for hot-work die steel.
In addition, it is noted that the density of the Fe-Mn-Al-C alloy of the present invention is about 6.6-6.8g/cm3Compared with the common die steel (the density is about 7.8-7.9 g/cm)3) The weight is 14 percent lighter. Therefore, the austenitic alloy steel of the present invention has advantages of light weight in addition to high strength and high ductility.
The prior art Fe-Mn-al-c alloys with high carbon content (1.4 wt.% to 2.2 wt.%) have a microstructure of the fully austenitic phase and very dense fine nano-sized (Fe, Mn) in the austenitic phase matrix despite process control (heat treatment/solutionizing/quenching)3AlCxCarbides (kappa' -carbides) and avoids coarse carbide precipitation at grain boundaries, and therefore, the iron-manganese-aluminum-carbon alloy has substantially good mechanical properties and elongation at room temperature. However, it has been found that when carbide strengthening elements (molybdenum, chromium, cobalt) are further added to the fe-mn-al-c alloy composition in a specific ratio in an amount of 2-6 wt.% in combination with the control of the heat treatment temperature, the disadvantage of coarse carbide precipitates, which generally greatly reduce the ductility of the material, generated on grain boundaries can be effectively avoided, and thus, the room temperature and high temperature strength of the fe-mn-al-c alloy steel can be further improved in addition to the ductility of the produced fe-mn-al-c alloy steel at room temperature, and in addition, the fe-al-mn-al-c alloy steel does not need to be subjected to the heat treatmentThe solution treatment step, therefore, can also effectively reduce the whole process time.
The properties of the austenitic alloy steels according to the present invention will be described in more detail below by making test pieces from the alloy compositions of examples 1 to 11 and comparative examples 1 to 3 and then performing the physical property tests.
It should be noted that the following specific examples are provided for illustrating the austenitic alloy steels according to the present invention, and the scope of the practice of the present invention should not be limited thereby.
Example 1
1. An alloy composition containing 30 wt.% manganese, 8.5 wt.% aluminum, 1.45 wt.% carbon, 6% molybdenum, and the balance iron was melted in a high frequency melting furnace at atmospheric air to form a casting having a thickness of 2 cm.
2. Heating the casting in a furnace at 1100 ℃ for 20 minutes, and then hot rolling at 1100 ℃ to 950 ℃ to a thickness of at least 25% less than the thickness of the casting to obtain a test piece.
3. The test piece is subjected to primary water quenching to room temperature, then the test piece is ground to remove an oxide layer, then Aging treatment (Aging) is carried out at 500 ℃, and finally the test piece is subjected to secondary water quenching to room temperature for later use.
Examples 2 to 11
The test pieces of the specific examples 2 to 11 were produced in the same manner as the test piece of the specific example 1 except for the contents of the respective elements in the alloy.
Comparative examples 1 to 3
The test pieces of comparative examples 1 to 3 were produced in the same manner as in example 1 except for the contents of the respective elements in the alloy.
The contents of the alloy constituent elements of the specific examples and comparative examples are summarized in Table 1.
TABLE 1
Next, the test pieces obtained in the above-mentioned examples and comparative examples were subjected to Yield Strength (YS), Ultimate Tensile Strength (UTS), elongation (El), and Rockwell hardness (HRc) tests.
The yield strength, ultimate tensile strength, elongation, and rockwell hardness of the test specimens were measured at room temperature in the following test manners, and the measurement results are shown in table 2.
Further, the test pieces of the above-mentioned examples 4, 7 and 9 and comparative examples 1 to 3 were subjected to the tests of yield strength and ultimate tensile strength at 300 ℃, 500 ℃ and 700 ℃ and the results are shown in Table 3.
Test modes of the respective characteristics:
1. tensile test
Yield Strength (Yield Strength, YS): the tensile plot is the stress at 0.2% strain parallel to the elastic strand.
Ultimate Tensile Strength (Ultimate Tensile Strength, UTS): maximum stress in the tensile plot.
Elongation (Elongation, El): the tensile curve plots the amount of strain parallel to the elastic line at the point of rupture.
The yield strength, ultimate tensile strength, and elongation were measured using an Instron tensile tester at room temperature (25 ℃ C.) at a tensile rate of 10-3The tensile curve is obtained by testing in seconds. The specification of the test piece refers to the specification of ASTM E8/E8M, and a high-temperature furnace is additionally arranged on a tensile testing machine during high-temperature testing, and the tensile testing is carried out after the high-temperature furnace is heated to a preset temperature.
2. Rockwell hardness test (HRc)
The test was carried out using a Rockwell Hardness machine (Rockwell Hardness machine) under a load of 150kgf using an indentor as a diamond cone.
TABLE 2
TABLE 3
As shown in table 2, the room temperature yield strength of the test specimens prepared in the examples 1 to 11 is 1230MPa to 1350MPa, the room temperature ultimate tensile strength is 1280MPa to 1386MPa, the room temperature elongation is 20% to 37%, and the rockwell hardness (HRc) is 45.0 to 47.7, which shows that the austenitic alloy steels according to the present invention indeed have high strength and also have good ductility, compared to the characteristic data of the comparative examples 1 and 2. It should be noted that, by controlling the content of molybdenum in the austenitic alloy steel to 2 wt.% to 6 wt.%, compared with the two existing hot work alloys of comparative examples 1 to 3 and AISI H13 and QRO 90, the austenitic alloy steel of the present invention not only maintains excellent room temperature strength and room temperature elongation, but also has a certain strength at high temperature, which shows that the austenitic alloy steel of the present invention has good ductility, and can be used as a novel hot work alloy steel, so that the cracking of the manufactured hot work tool during use can be avoided.
Preferably, the austenitic alloy steel has a carbon content of 1.42 wt.% to 1.5 wt.%, a molybdenum content of 3.5 wt.% to 5 wt.%, an ultimate tensile strength of 1353MPa to 1386MPa, a yield strength of 1310MPa to 1340MPa, and a rockwell hardness of 47 to 47.7.
More preferably, the carbon content of the austenitic alloy steel is between 1.42 wt.% and 1.45 wt.%, the molybdenum content is between 3.5 wt.% and 4 wt.%, and the elongation of the austenitic alloy steel can reach 25%.
Preferably, the manganese content of the austenitic alloy steel is between 27.7 wt.% and 30 wt.%, the aluminum content is between 8.2 wt.% and 8.5 wt.%, the ultimate tensile strength of the austenitic alloy steel can reach 1280MPa to 1386MPa, the yield strength can reach 1250MPa to 1350MPa, the Rockwell hardness can reach 46.7 to 47.7, and the elongation can reach 20% to 32%.
Preferably, the austenitic alloy steel has a manganese content of between 27 wt.% and 29 wt.%, an aluminum content of between 8.0 wt.% and 8.5 wt.%, and a molybdenum content of between 3.0 wt.% and 6 wt.%, the austenitic alloy steel may have an elongation of greater than 20%, a room temperature ultimate tensile strength of greater than 1280MPa, a yield strength of greater than 1230MPa, and both an ultimate tensile strength and a yield strength at 300 ℃ of greater than 1000 MPa.
Preferably, the austenitic alloy steel has a molybdenum content of 3.0 wt.% and contains 3 wt.% of chromium or 2 wt.% of cobalt, and has an ultimate tensile strength of 1280 to 1344MPa, a yield strength of 1230 to 1300MPa, a rockwell hardness of 45 to 46.8, and an elongation of 24 to 37% at room temperature.
In addition, it is noted that the mechanical strength data in table 2 show that the aging time of the above-mentioned examples 1 to 11 is 5 to 12 hours, which has no significant influence on the final mechanical strength, and it is shown that the present invention can effectively prevent the precipitation of coarse carbides by controlling the heat treatment temperature, thereby providing a large elasticity to the aging time without the problem of ductility reduction caused by the precipitation of coarse carbides being more significant as the aging time is longer than the known fe-mn-al-c steel.
Referring to FIGS. 2-4, FIGS. 2-4 are optical micrographs of the examples 1, 3 and 8 after heat treatment, and FIGS. 5-7 are optical micrographs of the examples 1, 3 and 8 after heat treatment and aging. As is clear from FIGS. 2 to 4, when the working temperature is controlled to 1100 ℃ to 950 ℃, coarse carbides are less likely to precipitate at the grain boundaries after the hot working treatment. Therefore, when further treated with different aging times, referring to fig. 5-7, coarse carbides are not easily generated. However, referring to FIGS. 8 and 9, FIGS. 8 and 9 are optical micrographs of the hot worked steel of comparative examples 1 and 2, and it is understood from FIGS. 8 and 9 that when the amount of the strong carbide forming element is excessively increased, a large amount of coarse carbides are precipitated even by controlling the temperature of the hot working, which is disadvantageous in the ductility of the Fe-Mn-Al-C alloy.
In addition, as can be seen from the high temperature tensile strength results in Table 3, the yield strength of the Fe-Al-Mn-C austenitic alloy steel prepared by the method is 970MPa to 1030MPa at 300 ℃, the ultimate tensile strength is 1022MPa to 1070MPa, the yield strength is 650MPa to 700MPa at 500 ℃, the ultimate tensile strength is 719MPa to 786MPa, the yield strength is 410MPa to 420MPa at 700 ℃, and the ultimate tensile strength is 440MPa to 449 MPa. In contrast, in comparative example 3, although the alloy has good ductility at room temperature, the yield strength and ultimate tensile strength at room temperature and high temperature (300 ℃ and 500 ℃) are not as good as those of the present invention, and the austenitic alloy steel of the present invention has good strength at room temperature and good mechanical strength at 300 ℃ and 500 ℃, and thus can be used as a novel medium-low temperature hot work alloy steel.
In summary, it is revealed by the prior art that adding a lower amount of a strong carbide forming element such as molybdenum or tungsten (e.g., Fe-29Mn-9Al-0.9C-0.6Mo, Fe-29Mn-9Al-0.9C-0.4Mo-0.6W, etc.) to an Fe-Mn-Al-C alloy with a carbon content of less than 1 wt.% improves the ductility of the alloy, but does not significantly improve the strength of the alloy, whereas adding a higher amount of the strong carbide forming element (e.g., Fe-27.9Mn-8.6Al-1.0C-0.51Mo-0.73W-0.55 Nb) to the Fe-Mn-Al-C alloy with a low carbon content increases the strength of the alloy but fails to maintain good ductility. The aforementioned us 9,528,177 patent also discloses that the addition of the strong carbide former to high carbon content ferro manganese aluminium carbon alloys is not effective in improving the ductility of the alloy and therefore does not suggest the addition of the strong carbide former to high carbon content ferro manganese aluminium carbon alloys. However, the austenitic alloy steel of the present invention can simultaneously have excellent mechanical strength and ductility at room temperature and maintain appropriate strength at high temperature by controlling the contents of each element in the high carbon content iron-manganese-aluminum-carbon alloy composition in a specific range and matching with a specific heat treatment temperature, and is lightweight and excellent in performance, and can be used as a steel material for machine parts and heat treatment tools, so that the austenitic alloy steel of the present invention can be used as a heat alloy steel in addition to a general steel material, and the object of the present invention can be achieved.
However, the above description is only an example of the present invention, and the scope of the present invention should not be limited by this, and all the simple equivalent changes and modifications made according to the claims and the contents of the patent specification should be included in the scope of the present invention.
Claims (19)
1. An austenitic alloy steel characterized by: comprises the following steps: 25 to 31 wt.% manganese, 7 to 10 wt.% aluminum, 1.2 to 1.6 wt.% carbon, greater than 0 to less than 6 wt.% molybdenum, and the balance iron.
2. The austenitic alloy steel of claim 1, wherein: the proportion of manganese ranges from 26 wt.% to 30 wt.%, and the proportion of aluminum ranges from 8 wt.% to 10 wt.%.
3. The austenitic alloy steel of claim 2, wherein: the manganese is present in a proportion of 27 to 29 wt.%, and the molybdenum is present in a proportion of 2 to 6 wt.%.
4. The austenitic alloy steel of claim 3, wherein: the proportion of aluminium is between 8 wt.% and 9 wt.%.
5. The austenitic alloy steel of claim 1, wherein: the proportion of carbon is 1.4 wt.% to 1.6 wt.%.
6. The austenitic alloy steel of claim 1, wherein: the proportion of molybdenum is between 2 wt.% and 6 wt.%.
7. The austenitic alloy steel of claim 1, wherein: also chromium is contained in a proportion of less than 6 wt.%.
8. The austenitic alloy steel of claim 1, wherein: cobalt is also included in a proportion of less than 5 wt.%.
9. The austenitic alloy steel of claim 1, wherein: the austenitic alloy steel is a complete austenite phase, and has an elongation of 20 to 40% at 25 ℃, an ultimate tensile strength of greater than 1250MPa, and an ultimate tensile strength of greater than 1000MPa at 300 ℃.
10. A manufacturing method of austenitic alloy steel is characterized by comprising the following steps: comprises the following steps:
step (a): melting the alloy composition of claim 1 into a casting;
step (b): performing hot working treatment on the casting at 1100-950 ℃ to form a hot-working piece;
step (c): carrying out primary water quenching on the hot work piece after the hot work treatment; and
step (d): and (3) carrying out aging treatment on the hot work piece subjected to the first water quenching at 480-600 ℃.
11. The method of making an austenitic alloy steel according to claim 10, wherein: the time of the aging treatment is 5 to 12 hours when the temperature of the aging treatment is 480 to 500 ℃, and the time of the aging treatment is 1 to 4 hours when the temperature of the aging treatment is more than 500 to 600 ℃.
12. The method of making an austenitic alloy steel according to claim 10, wherein: and (e) carrying out secondary water quenching on the aged hot work piece.
13. The method of making an austenitic alloy steel according to claim 10, wherein: said step (b) is heat treating said casting to a thickness of at least 25% less than the thickness of said casting.
14. An austenitic alloy steel made according to the method of claim 10, wherein: the austenitic alloy steel has an elongation of 20 to 40% at room temperature and an ultimate tensile strength of greater than 1000MPa at 300 ℃.
15. The austenitic alloy steel of claim 14, wherein: the yield strength of the austenitic alloy steel at room temperature is 1230-1350 MPa, and the ultimate tensile strength is 1280-1386 MPa.
16. The austenitic alloy steel of claim 14, wherein: the austenitic alloy steel has a Rockwell hardness at room temperature of between 45 and 48.
17. The austenitic alloy steel of claim 14, wherein: the yield strength of the austenitic alloy steel at 300 ℃ is more than 970 MPa.
18. The austenitic alloy steel of claim 14, wherein: the yield strength of the austenitic alloy steel at 500 ℃ is more than 650MPa, and the ultimate tensile strength is more than 700 MPa.
19. The austenitic alloy steel of claim 14, wherein: the austenitic alloy steel has a yield strength of 410 to 420MPa and an ultimate tensile strength of 440 to 449MPa at 700 ℃.
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Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20130240520A1 (en) * | 2010-11-26 | 2013-09-19 | Salzgitter Flachstahl Gmbh | Energy-storing container made of lightweight steel |
| CN106244927A (en) * | 2016-09-30 | 2016-12-21 | 北京理工大学 | A kind of low-density unimach and preparation method thereof |
Family Cites Families (24)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB841366A (en) * | 1957-07-02 | 1960-07-13 | Langley Alloys Ltd | Improvements in iron aluminium alloys |
| US4865662A (en) * | 1987-04-02 | 1989-09-12 | Ipsco Inc. | Aluminum-manganese-iron stainless steel alloy |
| GB2220674A (en) * | 1988-06-29 | 1990-01-17 | Nat Science Council | Alloys useful at elevated temperatures |
| US4975335A (en) * | 1988-07-08 | 1990-12-04 | Fancy Steel Corporation | Fe-Mn-Al-C based alloy articles and parts and their treatments |
| US4875933A (en) * | 1988-07-08 | 1989-10-24 | Famcy Steel Corporation | Melting method for producing low chromium corrosion resistant and high damping capacity Fe-Mn-Al-C based alloys |
| FR2634221A1 (en) * | 1988-07-13 | 1990-01-19 | Nat Science Council | Cast articles made of alloys based on Fe-Mn-Al-Cr-Si-C |
| CA1334802C (en) * | 1989-03-02 | 1995-03-21 | James M. Zimmer | Aluminum-manganese-iron steel alloy |
| JPH02228450A (en) * | 1989-03-02 | 1990-09-11 | Tokushu Denkyoku Kk | Casting alloy |
| KR920702870A (en) * | 1989-08-31 | 1992-10-28 | 죤 콤리 | Aluminum-manganese-iron steel alloy |
| JPH0699775B2 (en) * | 1991-12-27 | 1994-12-07 | 東大精密鋳造股▲フン▼有限公司 | Precision casting method for iron-manganese-aluminum alloy |
| US5167733A (en) * | 1992-02-06 | 1992-12-01 | Eastern Precision Casting Co., Ltd. | Method for manufacturing iron-manganese-aluminum alloy castings |
| JP4235077B2 (en) | 2003-06-05 | 2009-03-04 | 新日本製鐵株式会社 | High strength low specific gravity steel plate for automobile and its manufacturing method |
| JP4179112B2 (en) * | 2003-09-08 | 2008-11-12 | ダイキン工業株式会社 | Equipment management device, equipment management system, and equipment management method |
| JP5317048B2 (en) * | 2008-06-10 | 2013-10-16 | 株式会社Ｎｅｏｍａｘマテリアル | Resistance alloy manufacturing method |
| US7931758B2 (en) * | 2008-07-28 | 2011-04-26 | Ati Properties, Inc. | Thermal mechanical treatment of ferrous alloys, and related alloys and articles |
| DE102011000089A1 (en) * | 2011-01-11 | 2012-07-12 | Thyssenkrupp Steel Europe Ag | Method for producing a hot rolled flat steel product |
| JP5177310B2 (en) * | 2011-02-15 | 2013-04-03 | Ｊｆｅスチール株式会社 | High tensile strength steel sheet with excellent low temperature toughness of weld heat affected zone and method for producing the same |
| TWI445832B (en) * | 2011-09-29 | 2014-07-21 | The composition design and processing methods of high strength, high ductility, and high corrosion resistance alloys | |
| WO2015099221A1 (en) * | 2013-12-26 | 2015-07-02 | 주식회사 포스코 | Steel sheet having high strength and low density and method of manufacturing same |
| US20170088910A1 (en) * | 2015-09-29 | 2017-03-30 | Exxonmobil Research And Engineering Company | Corrosion and cracking resistant high manganese austenitic steels containing passivating elements |
| WO2017061487A1 (en) * | 2015-10-06 | 2017-04-13 | 新日鐵住金株式会社 | Austenitic stainless steel sheet |
| US10227681B2 (en) * | 2015-10-21 | 2019-03-12 | Caterpillar Inc. | High manganese steel with enhanced wear and impact characteristics |
| WO2017203312A1 (en) * | 2016-05-24 | 2017-11-30 | Arcelormittal | Cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts |
| KR101836714B1 (en) * | 2016-10-12 | 2018-03-09 | 현대자동차주식회사 | High manganese steel |
-
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20130240520A1 (en) * | 2010-11-26 | 2013-09-19 | Salzgitter Flachstahl Gmbh | Energy-storing container made of lightweight steel |
| CN106244927A (en) * | 2016-09-30 | 2016-12-21 | 北京理工大学 | A kind of low-density unimach and preparation method thereof |
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