CN116043136A - Low-expansion high-strength alloy steel and manufacturing method and application thereof - Google Patents
Low-expansion high-strength alloy steel and manufacturing method and application thereof Download PDFInfo
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- CN116043136A CN116043136A CN202310057521.XA CN202310057521A CN116043136A CN 116043136 A CN116043136 A CN 116043136A CN 202310057521 A CN202310057521 A CN 202310057521A CN 116043136 A CN116043136 A CN 116043136A
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- 229910000851 Alloy steel Inorganic materials 0.000 title claims abstract description 74
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 238000005266 casting Methods 0.000 claims abstract description 22
- 239000000126 substance Substances 0.000 claims abstract description 19
- 230000032683 aging Effects 0.000 claims abstract description 13
- 238000005097 cold rolling Methods 0.000 claims abstract description 12
- 238000005098 hot rolling Methods 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910000831 Steel Inorganic materials 0.000 claims description 22
- 239000010959 steel Substances 0.000 claims description 22
- 238000010438 heat treatment Methods 0.000 claims description 12
- 238000005096 rolling process Methods 0.000 claims description 8
- 238000000265 homogenisation Methods 0.000 claims description 7
- 238000001816 cooling Methods 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 claims description 6
- 238000003723 Smelting Methods 0.000 claims description 4
- 230000009467 reduction Effects 0.000 claims description 4
- 239000002253 acid Substances 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 238000002791 soaking Methods 0.000 claims description 3
- 238000005406 washing Methods 0.000 claims description 3
- 238000000034 method Methods 0.000 abstract description 4
- 230000008569 process Effects 0.000 abstract description 4
- 239000010955 niobium Substances 0.000 description 13
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 229910000765 intermetallic Inorganic materials 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 6
- 239000011159 matrix material Substances 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 5
- 238000013461 design Methods 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000011161 development Methods 0.000 description 3
- 230000018109 developmental process Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000002360 preparation method Methods 0.000 description 3
- 229910001374 Invar Inorganic materials 0.000 description 2
- 229910017709 Ni Co Inorganic materials 0.000 description 2
- 229910003267 Ni-Co Inorganic materials 0.000 description 2
- 229910003262 Ni‐Co Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000004321 preservation Methods 0.000 description 2
- 229910020630 Co Ni Inorganic materials 0.000 description 1
- 229910004298 SiO 2 Inorganic materials 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000005495 investment casting Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/007—Heat treatment of ferrous alloys containing Co
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/02—Hardening by precipitation
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- Heat Treatment Of Steel (AREA)
Abstract
The present invention relates to a kind ofLow expansion high strength alloy steel and its manufacturing method and application. The chemical components in percentage by mass are as follows: 22% or more of Co or less than 29%,20% or less of Ni or less than 28%,1.0% or less of Nb or less than 4.5%,1.0% or less of Cr or less than 3.5%, 2.0% or less of Al, 1.0% or less of Ti, 0.6% or less of Si, and the balance of Fe and unavoidable impurity elements. The low-expansion high-strength alloy steel is prepared by the technological processes of casting, homogenizing, hot rolling, cold rolling and aging treatment. The linear expansion coefficient alpha of the low-expansion high-strength alloy steel m (20,400)≤9.6×10 ‑6 And the room temperature hardness of the alloy steel is more than or equal to 42HRC.
Description
Technical Field
The invention belongs to the technical field of alloy steel, in particular relates to the technical field of precision die steel, and specifically relates to low-expansion high-strength alloy steel and a manufacturing method and application thereof.
Background
With the development of modern industry, the mold is widely applied to products such as automobiles, household appliances, telecommunication, instruments and meters, aerospace, medical appliances and the like, wherein about eight parts are required to be processed and molded by the mold. The precision die is a special die for precision casting, has very high precision requirement, reaches micron level at present, and needs precision machining equipment and a redundant machining process flow to ensure the quality of products, so that the cost is greatly increased. The development of precision die manufacturing technology is limited by the physical and mechanical properties of die steel, and the characteristics of die steel directly affect the design and production of precision die products.
At present, most of precision die manufacturing adopts die steel such as S136, H13 and the like, and the steel has higher polishing property and corrosion resistance, and has certain strength and hardness, thus being a main die use material at present. However, as the die steel has higher linear expansion coefficient in the service temperature range, the deviation of the product and the design size produced by the die is caused, the deviation of the size must be compensated by the reverse size compensation design, and particularly the die product with a high complex shape cavity is produced, and the precision of the finished product is not ensured due to the thermal deformation in the production process; therefore, the above limitations lead to increased difficulty in designing and producing high-precision dies, and greatly reduced yields of precision products, thereby greatly increasing the manufacturing and use costs of the dies. Therefore, designing a high-strength alloy steel with stable low thermal expansion coefficient is a necessary condition for the development of the future precision die industry.
Disclosure of Invention
The invention aims to solve the technical problem of high thermal expansion coefficient of the existing precision die steel, and provides low-expansion high-strength alloy steel, and a manufacturing method and application thereof.
The aim of the invention can be achieved by the following technical scheme:
the first aspect of the present invention provides a low expansion high strength alloy steel.
To obtain a low expansion coefficient, invar is used as a matrix for the alloy steel. In the invention, co and Ni elements are added, so that the alloy steel matrix has higher Curie temperature point and stable low linear expansion coefficient.
In order to obtain high strength properties, the matrix of the alloy steel needs to be relatively uniformly dispersed with the fine intermetallic compounds, and the intermetallic compounds do not coarsen significantly when the alloy steel is used for a long period of time in an environment of 400 ℃. Proper amounts of Nb, ti and Al intermetallic compound forming elements are added into the steel, and part of Ni is combined with Nb, ti and Al through aging treatment, so that gamma 'and gamma' intermetallic compounds are formed in Fe-Ni-Co alloy crystals, and the strength of the steel is improved. The intermetallic compound with small size has good thermal stability at 400 ℃ and can keep the strength of alloy steel from being changed obviously.
In order to provide the alloy steel with good high-temperature oxidation resistance, the alloying elements contain Si and Cr elements. By forming dense Cr on the surface of steel 2 O 3 、SiO 2 Or a composite oxide layer, which reduces the oxidation rate of the steel at high temperatures.
In order to make alloy steel have good wear resistance and hot hardness, a proper amount of Cr element is required to be added.
Specifically, the low-expansion high-strength alloy steel provided by the invention comprises the following chemical components, by mass, 22% -29% of Co, 20% -28% of Ni, 1.0% -4.5% of Nb, 1.0% -3.5% of Cr, 2.0% of Al, 1.0% of Ti, 0.6% of Si and the balance of Fe and unavoidable impurity elements.
Preferably, the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 2.0 to 3.0 percent.
Preferably, the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 1.0 to 2.0 percent.
Preferably, the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 0.5 to 0.9 percent.
Preferably, the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 0.4 to 0.6 percent.
Preferably, the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 2.0 to 3.0 percent of Al with the mass percent as follows: 1.0 to 2.0 percent of Ti in percentage by mass: 0.5 to 0.9 percent of Si in percentage by mass: 0.4 to 0.6 percent.
The room-temperature hardness of the low-expansion high-strength alloy steel is more than or equal to 42HRC; the average linear expansion coefficient is less than or equal to 9.6X10 at the temperature of 20-400 DEG C -6 /℃。
In the composition design of the present invention, the functions of the respective components are as follows.
Co: co can effectively reduce the linear expansion coefficient of alloy steel and expand the temperature range of low expansion property, and promote the precipitation of a precipitated phase gamma' phase. The Co content range is determined to be 22% -29% by comprehensively considering the cost of Co.
Ni: suitable Ni content ensures the alloy steel has a tiling effect and maintains a low expansion coefficient. Meanwhile, ni is used as an austenite expanding region and austenite stabilizing element, so that the alloy steel can obtain a single-phase austenite structure at room temperature, the Ms point is reduced, the corrosion resistance of the alloy steel is improved, and the application range of the alloy steel is widened. In addition, ni can also form intermetallic compound reinforced alloy matrix with other metallic elements, e.g. Ni 3 (Al, ti). The invention comprehensively considers the effective range of the tile effect and the influence of the addition of other alloy elements, and determines the range of Ni content to be 20% -28%.
Ti, al: as the main strengthening phase forming element of the invention, a proper amount of Ti and Al are added to form gamma' (Ni during aging 3 (Ti, al)) intermetallic compounds. The alloy steel has higher strength and hardness due to the precipitation strengthening effect of the gamma' phase. However, when the Al content is too large, the linear expansion coefficient of the alloy steel is greatly increased. In addition, when the Ti content is excessive, formation of a detrimental phase, such as η phase, is caused. The invention comprehensively considers that the content of Al is 1% -2% and the content of Ti is less than or equal to 1%. The preferred Al content is in the range of 1.0% to 2.0%, and the preferred Ti content is in the range of 0.5% to 0.9%.
Nb: according to the invention, by adding a proper amount of niobium into alloy components, the precipitation of gamma ' (Ni 3 Nb) strengthening phases of the alloy steel is completed in the aging process, meanwhile, the precipitation of gamma ' strengthening phases is promoted, the aggregation growth of gamma ' phases is delayed, and the strength of the alloy steel is further improved. However, excessive Nb content also leads to formation of eta phase. The invention comprehensively considers that the Nb content range is 1% -4.5%.
Cr: the addition of Cr can effectively improve the wear resistance and the hot hardness of alloy steel, and meanwhile, the Cr element dissolved in austenite can improve the strength, the corrosion resistance and the oxidation resistance of the steel, so that the application range of the alloy steel is enlarged. However, excessive addition of Cr can greatly improve the linear expansion coefficient of the alloy steel, and the content range of Cr is 2.0-3.5% by comprehensive consideration. The preferable range of Cr content is 2.0% to 3.0%.
Si: si also plays a solid solution strengthening role, and improves the solidification performance of alloy steel. However, the addition of excessive Si greatly increases the linear expansion coefficient of the alloy steel, so that the Si content of the present invention should be controlled to 0.6% or less. The preferable Si content is in the range of 0.4% to 0.6%.
Further, the room temperature hardness of the low-expansion high-strength alloy steel is more than or equal to 42HRC; the average linear expansion coefficient is less than or equal to 9.6X10 at the temperature of 20-400 DEG C -6 /℃。
In a second aspect, the invention provides a preparation method of the low-expansion high-strength alloy steel, which is prepared through the technological processes of casting, homogenizing, hot rolling, cold rolling and aging treatment.
Preferably, the preparation method comprises the following steps:
step 1: smelting and casting according to the following components to obtain a casting blank
22% or less of Co or less than 29%,20% or less of Ni or less than 28%,1.0% or less of Nb or less than 4.5%,1.0% or less of Cr or less than 3.5%, 2.0% or less of Al, 1.0% or less of Ti, 0.6% or less of Si, and the balance of Fe and unavoidable impurity elements;
step 2: homogenization treatment
Heating the casting blank at 1100-1180 ℃ for 20-30 hours, and air cooling the casting blank to room temperature after homogenization treatment;
step 3: hot rolling
Heating a casting blank at 1000-1250 ℃ for 0.5-3 hours, hot-rolling the casting blank into a hot-rolled plate, wherein the hot-rolled deformation is more than or equal to 75%, and the final rolling temperature is more than or equal to 900 ℃;
step 4: acid washing
Step 5: cold rolling
Cold rolling the pickled hot-rolled plate, wherein the rolling reduction is more than or equal to 10%, so as to obtain a cold-rolled plate;
step 6: aging after cold rolling
Heating the cold-rolled sheet to a soaking temperature of 600-700 ℃ for 1-10 h; and cooling the steel plate to room temperature after aging.
The invention further provides application of the low-expansion high-strength alloy steel, which is suitable for manufacturing high-precision dies.
Compared with the prior art, the invention adopts invar alloy as a matrix, and Co and Ni elements are added, so that the alloy steel matrix has higher Curie temperature point and stable low linear expansion coefficient, a proper amount of Nb, ti and Al intermetallic compounds are added into the steel to form elements, and part of Ni is combined with Nb, ti and Al through aging treatment, and gamma' intermetallic compounds are formed in Fe-Ni-Co alloy crystals, thereby improving the strength of the steel.
After heat treatment, the high-strength alloy steel of the invention has an average linear expansion coefficient alpha of 20-400 DEG C m (20,400)≤9.6×10 -6 And the room temperature hardness is more than or equal to 42HRC at the temperature of/DEG C. Experiments prove that the novel low-expansion high-strength alloy steel has the characteristics of high strength and low linear expansion coefficient compared with the existing alloy system.
Compared with the traditional die steel, the high-strength alloy steel has the advantages of good wear resistance, thermal stability and corrosion resistance while keeping stable low expansion characteristic.
In addition, the manufacturing process related to the invention can be completed on the existing alloy steel production line without great adjustment. Therefore, the invention has good popularization and application prospect.
Detailed Description
The low-expansion high-strength alloy steel comprises the following chemical components of 22% or more of Co or less than 29%,20% or less of Ni or less than 28%,1.0% or less of Nb or less than 4.5%,1.0% or less of Cr or less than 3.5%, 2.0% or less of Al, 1.0% or less of Ti, 0.6% or less of Si, and the balance of Fe and unavoidable impurity elements.
Preferably, the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 2.0 to 3.0 percent.
Preferably, the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 1.0 to 2.0 percent.
Preferably, the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 0.5 to 0.9 percent.
Preferably, the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 0.4 to 0.6 percent.
The preparation method of the low-expansion high-strength alloy steel comprises the following steps:
step 1: smelting and casting according to the following components to obtain a casting blank
22% or less of Co or less than 29%,20% or less of Ni or less than 28%,1.0% or less of Nb or less than 4.5%,1.0% or less of Cr or less than 3.5%, 2.0% or less of Al, 1.0% or less of Ti, 0.6% or less of Si, and the balance of Fe and unavoidable impurity elements;
step 2: homogenization treatment
Heating the casting blank at 1100-1180 ℃ for 20-30 hours, and air cooling the casting blank to room temperature after homogenization treatment;
step 3: hot rolling
Heating a casting blank at 1000-1250 ℃ for 0.5-3 hours, hot-rolling the casting blank into a hot-rolled plate, wherein the hot-rolled deformation is more than or equal to 75%, and the final rolling temperature is more than or equal to 900 ℃;
step 4: acid washing
Step 5: cold rolling
Cold rolling the pickled hot-rolled plate, wherein the rolling reduction is more than or equal to 10%, so as to obtain a cold-rolled plate;
step 6: aging after cold rolling
Heating the cold-rolled sheet to a soaking temperature of 600-700 ℃ for 1-10 h; and cooling the steel plate to room temperature after aging.
The present invention will be described in detail with reference to specific examples.
Table 1 shows the mass percentages of the chemical components of the alloy steels of the examples and comparative examples according to the present invention, and Table 2 shows the heat treatment process and the corresponding average linear expansion coefficient alpha of the alloy steels of the examples and comparative examples according to the present invention m (20,400) and room temperature hardness.
The content ratios of the respective components in examples 1 to 8 and comparative examples 1 to 2 were designed according to Table 1.
TABLE 1 (Unit: wt%)
| Co | Ni | Nb | Cr | Al | Ti | Si | Fe | |
| Example 1 | 22.1 | 27.4 | 4.45 | 2.88 | 1.92 | 0.87 | 0.51 | Allowance of |
| Example 2 | 23.4 | 25.9 | 4.21 | 2.49 | 1.76 | 0.85 | 0.49 | Allowance of |
| Example 3 | 24.7 | 25.1 | 3.78 | 1.27 | 1.65 | 0.84 | 0.09 | Allowance of |
| Example 4 | 25.1 | 24.6 | 2.85 | 2.58 | 0.13 | 0.34 | 0.26 | Allowance of |
| Example 5 | 25.5 | 23.1 | 4.01 | 3.08 | 1.48 | 0.79 | 0.57 | Allowance of |
| Example 6 | 26.9 | 22.6 | 3.07 | 2.69 | 0.89 | 0.49 | 0.56 | Allowance of |
| Example 7 | 27.3 | 21.9 | 1.43 | 2.39 | 0.91 | 0.12 | 0.59 | Allowance of |
| Example 8 | 28.9 | 20.4 | 2.76 | 2.12 | 0.21 | 0.65 | 0.52 | Allowance of |
| Comparative example 1 | 26.1 | 23.4 | 0.79 | 2.13 | 1.21 | 0.91 | 0.52 | Allowance of |
| Comparative example 2 | 20.3 | 25.9 | 3.87 | 2.33 | 2.98 | 0.85 | 0.52 | Allowance of |
The steel having the composition shown in table 1 was manufactured into slabs after smelting and casting. After homogenization treatment of heat preservation for 20h at 1160 ℃, heating the slab at 1150 ℃, hot-rolling the slab after heat preservation for 2h, finishing hot-rolling finish rolling at 900 ℃, and hot-rolling accumulated deformation exceeding 75%. After pickling, the hot-rolled sheet was cold-rolled, and the rolling reduction was more than 10%. Examples 1 to 8 and comparative examples 1 to 2, and the corresponding linear expansion coefficients alpha m (20,400) and room temperature hardness are shown in Table 2.
TABLE 2
As can be seen from Table 2, the present invention can obtain high strength alloy steel with low thermal expansion characteristics by reasonable composition and process design, and the average linear expansion coefficient alpha m (20,400)≤9.6×10 -6 And the room temperature hardness of the alloy steel is more than or equal to 42HRC.
Therefore, compared with the traditional die steel, the high-strength alloy steel has better wear resistance, thermal stability and corrosion resistance while keeping stable low expansion characteristic.
In addition, the manufacturing process related to the invention can be completed on the existing alloy steel production line without great adjustment. Therefore, the invention has good popularization and application prospect.
The previous description of the embodiments is provided to facilitate a person of ordinary skill in the art in order to make and use the present invention. It will be apparent to those skilled in the art that various modifications can be readily made to these embodiments and the generic principles described herein may be applied to other embodiments without the use of the inventive faculty. Therefore, the present invention is not limited to the above-described embodiments, and those skilled in the art, based on the present disclosure, should make improvements and modifications without departing from the scope of the present invention.
Claims (10)
1. A low-expansion high-strength alloy steel is characterized in that the mass fraction of the chemical components is 22% -29% Co, 20% -28% Ni, 1.0% -4.5% Nb, 1.0% -3.5% Cr, 2.0% Al, 1.0% Ti, 0.6% Si and the balance Fe and unavoidable impurity elements.
2. The low-expansion high-strength alloy steel according to claim 1, wherein the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 2.0 to 3.0 percent.
3. The low-expansion high-strength alloy steel according to claim 1, wherein the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 1.0 to 2.0 percent.
4. The low-expansion high-strength alloy steel according to claim 1, wherein the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 0.5 to 0.9 percent.
5. The low-expansion high-strength alloy steel according to claim 1, wherein the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 0.4 to 0.6 percent.
6. The low-expansion high-strength alloy steel according to claim 1, wherein the low-expansion high-strength alloy steel comprises the following chemical components in percentage by mass: 2.0 to 3.0 percent of Al with the mass percent as follows: 1.0 to 2.0 percent of Ti in percentage by mass: 0.5 to 0.9 percent of Si in percentage by mass: 0.4 to 0.6 percent.
7. The low-expansion high-strength alloy steel according to claim 1, wherein the low-expansion high-strength alloy steel has a room-temperature hardness of 42HRC or more; the average linear expansion coefficient is less than or equal to 9.6X10 at the temperature of 20-400 DEG C -6 /℃。
8. The method for producing a low-expansion high-strength alloy steel according to any one of claims 1 to 7, which is characterized by comprising the steps of casting, homogenizing, hot rolling, cold rolling and aging.
9. The method for producing a low expansion high strength alloy steel according to claim 8, comprising the steps of:
step 1: smelting and casting according to the following components to obtain a casting blank
22% or less of Co or less than 29%,20% or less of Ni or less than 28%,1.0% or less of Nb or less than 4.5%,1.0% or less of Cr or less than 3.5%, 2.0% or less of Al, 1.0% or less of Ti, 0.6% or less of Si, and the balance of Fe and unavoidable impurity elements;
step 2: homogenization treatment
Heating the casting blank at 1100-1180 ℃ for 20-30 hours, and air cooling the casting blank to room temperature after homogenization treatment;
step 3: hot rolling
Heating a casting blank at 1000-1250 ℃ for 0.5-3 hours, hot-rolling the casting blank into a hot-rolled plate, wherein the hot-rolled deformation is more than or equal to 75%, and the final rolling temperature is more than or equal to 900 ℃;
step 4: acid washing
Step 5: cold rolling
Cold rolling the pickled hot-rolled plate, wherein the rolling reduction is more than or equal to 10%, so as to obtain a cold-rolled plate;
step 6: aging after cold rolling
Heating the cold-rolled sheet to a soaking temperature of 600-700 ℃ for 1-10 h; and cooling the steel plate to room temperature after aging.
10. Use of a low expansion high strength alloy steel according to any one of claims 1 to 7, wherein said low expansion high strength alloy steel is suitable for manufacturing high precision moulds.
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| CN1053094A (en) * | 1989-12-15 | 1991-07-17 | 英科合金国际有限公司 | Oxidation resistant low expansion superalloys |
| US5192497A (en) * | 1990-12-18 | 1993-03-09 | Hitachi Metals, Ltd. | Superalloys with low thermal-expansion coefficient |
| TW200400272A (en) * | 2002-06-18 | 2004-01-01 | Nippon Kokan Kk | Low thermal expansion alloy sheet and method for manufacturing the same |
| US20190048433A1 (en) * | 2015-09-29 | 2019-02-14 | Hitachi Metals, Ltd. | Low thermal expansion superalloy and manufacturing method thereof |
| CN111809120A (en) * | 2020-07-21 | 2020-10-23 | 中国科学院金属研究所 | Low-expansion alloy and preparation method thereof |
| CN115029641A (en) * | 2022-07-25 | 2022-09-09 | 西安稀有金属材料研究院有限公司 | Fixed expansion alloy plate with good plasticity and preparation method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN1053094A (en) * | 1989-12-15 | 1991-07-17 | 英科合金国际有限公司 | Oxidation resistant low expansion superalloys |
| US5192497A (en) * | 1990-12-18 | 1993-03-09 | Hitachi Metals, Ltd. | Superalloys with low thermal-expansion coefficient |
| TW200400272A (en) * | 2002-06-18 | 2004-01-01 | Nippon Kokan Kk | Low thermal expansion alloy sheet and method for manufacturing the same |
| US20190048433A1 (en) * | 2015-09-29 | 2019-02-14 | Hitachi Metals, Ltd. | Low thermal expansion superalloy and manufacturing method thereof |
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