CN114250422B - Die steel with good toughness and high thermal conductivity and preparation method thereof - Google Patents
Die steel with good toughness and high thermal conductivity and preparation method thereof Download PDFInfo
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- CN114250422B CN114250422B CN202111673677.8A CN202111673677A CN114250422B CN 114250422 B CN114250422 B CN 114250422B CN 202111673677 A CN202111673677 A CN 202111673677A CN 114250422 B CN114250422 B CN 114250422B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D31/00—Cutting-off surplus material, e.g. gates; Cleaning and working on castings
- B22D31/002—Cleaning, working on castings
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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
- 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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- 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
- C21D6/001—Heat treatment of ferrous alloys containing Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Abstract
The invention discloses die steel with good toughness and high heat conductivity, which comprises the following components in percentage by weight: 0.04-0.06% of C, 0.7-0.8% of Ni, 1.4-1.6% of Cu, 0.65-0.75% of Mn, 0.35-0.45% of Si, 2.8-3.2% of Mo, 1.8-2.2% of W and the balance of Fe. The invention also discloses a preparation method of the die steel with good toughness and high thermal conductivity, which comprises the following steps: s1, taking the raw materials, smelting and casting to obtain a casting with the same component ratio as the die steel with good toughness and high heat conductivity; s2, carrying out solid solution treatment on the casting, quenching, and carrying out heat preservation and aging treatment at 475-. The die steel has high heat conductivity and good toughness and strength.
Description
Technical Field
The invention relates to the technical field of alloy, in particular to die steel with good toughness and high heat conductivity and a preparation method thereof.
Background
The mold is called as 'master of industry' and is widely applied in the fields of electronics, automobiles, motors, electrical appliances, instruments, household appliances, communication and the like, and the level of the mold manufacturing technology is directly related to the capability of a country for researching, developing and producing and manufacturing industrial products. With the rapid development of science and technology and the increasing improvement of living standard of people, social groups put higher demands on products manufactured by moulds. The high-thermal-conductivity die steel can improve the production efficiency of the die and realize the improvement of the production efficiency.
The H13 steel is hot work die steel, and the grade is 4Cr5MoSiV 1. At present, in the traditional processing field, a typical high thermal conductivity die steel adopts a low alloying design idea, on the basis of H13 steel, the addition of Si and Cr alloy elements which remarkably deteriorate the thermal conductivity is reduced, and the performance of high thermal conductivity is finally obtained, however, the steels are medium carbon steels with about 0.4 percent (wt%) of carbon content, and the steel is strengthened by carbide, so that the toughness of the steel is low, and the formability of the material is poor.
Disclosure of Invention
Based on the technical problems in the background art, the invention provides the die steel with good toughness and high thermal conductivity and the preparation method thereof; the die steel has high heat conductivity and good toughness and strength.
The invention provides die steel with good toughness and high heat conductivity, which comprises the following components in percentage by weight: 0.04-0.06% of C, 0.7-0.8% of Ni, 1.4-1.6% of Cu, 0.65-0.75% of Mn, 0.35-0.45% of Si, 2.8-3.2% of Mo, 1.8-2.2% of W and the balance of Fe.
Preferably, the components thereof comprise, in weight percent: 0.05% of C, 0.75% of Ni, 1.5% of Cu, 0.7% of Mn, 0.4% of Si, 3% of Mo, 2% of W and the balance of Fe.
The invention also provides a preparation method of the die steel with good toughness and high thermal conductivity, which comprises the following steps:
s1, taking the raw materials, smelting and casting to obtain a casting with the same component ratio as the die steel with good toughness and high heat conductivity;
s2, carrying out solid solution treatment on the casting, quenching, and carrying out heat preservation and aging treatment at 475-.
Preferably, in S2, the solid solution temperature is not less than 950 ℃, and the solid solution time is not less than 30 min.
Preferably, in S2, the heat preservation and aging treatment is carried out at 475-525 ℃ for 2-8 h.
Preferably, in S2, the heat preservation and aging treatment is carried out for 4h at 500 ℃.
Preferably, in S2, the ingot is quenched with water to room temperature.
Preferably, in S2, after aging, the die steel with good toughness and high thermal conductivity is obtained by air cooling to room temperature.
Has the advantages that:
the invention reduces the carbon content, the alloy content and the elements in proper proportion, so that the alloy material has good toughness and strength and higher thermal conductivity; the addition of a proper amount of W and Si elements ensures that the ferrite accounts for a smaller proportion in the cast structure of the alloy powder; and because the carbon content is low, most of W element exists in the form of solid solution in steel, thereby improving the hardenability of alloy material castings.
Drawings
FIG. 1 is a metallographic structure diagram of a casting in example 4.
FIG. 2 is a metallographic structure of the die steel aged at different aging temperatures for 4 hours in example 4, wherein a is 425 ℃, b is 450 ℃, c is 475 ℃, d is 500 ℃, e is 525 ℃, f is 550 ℃ and g is 575 ℃.
FIG. 3 is a metallographic structure of a die steel aged at 500 ℃ for different times in example 4, wherein the metallographic structure sequentially comprises solid solution + aging for 0h, solid solution + aging for 0.5h, solid solution + aging for 1h, and solid solution + aging for 4h from left to right.
Detailed Description
The technical solution of the present invention will be described in detail below with reference to specific examples.
The tensile property test is carried out by using an AGXplus electronic universal testing machine with the specification of 20Kn produced by Jinshima according to the national standard GB/T228-2002 indoor tensile test method for metal materials.
A hardness measuring instrument is an HVS-1000A type hardness tester, and a hardness measuring experiment is carried out according to the standard GB/T230 Rockwell hardness test of metal materials.
Example 1
The die steel with good toughness and high thermal conductivity comprises the following components in percentage by weight: 0.04% of C, 0.8% of Ni, 1.4% of Cu, 0.75% of Mn, 0.35% of Si, 3.2% of Mo, 1.8% of W and the balance of Fe.
Example 2
The die steel with good toughness and high thermal conductivity comprises the following components in percentage by weight: 0.06% of C, 0.7% of Ni, 1.6% of Cu, 0.65% of Mn, 0.45% of Si, 2.8% of Mo, 2.2% of W and the balance of Fe.
Example 3
The die steel with good toughness and high thermal conductivity comprises the following components in percentage by weight: 0.05% of C, 0.75% of Ni, 1.5% of Cu, 0.7% of Mn, 0.4% of Si, 3% of Mo, 2% of W and the balance of Fe.
Example 4
A preparation method of die steel with good toughness and high heat conductivity comprises the following steps:
s1, taking the raw materials, and carrying out smelting and casting to obtain a casting of the die steel with good component ratio and good toughness and high thermal conductivity in the embodiment 3;
s2, placing the casting at 950 ℃ for solid solution for 30min, then quenching the casting to room temperature by water, carrying out aging treatment, and then air cooling to room temperature to obtain the die steel with good toughness and high heat conductivity.
The properties of the die steel under different aging conditions were examined, and the results are shown in tables 1 to 3 and FIGS. 1 to 3.
FIG. 1 is a metallographic structure drawing of a casting in example 4.
As can be seen from fig. 1: obvious defects such as air holes and cracks are not found in the casting, the smelted structure is very compact, the casting is composed of white ferrite and gray martensite, the ferrite exists in a strip needle-shaped form, the proportion of the ferrite in the casting is less, probably because the alloy material contains a proper amount of Mo, W and Si elements, and under the condition that the carbon content of the alloy is very low, the hardenability of the material is greatly improved by the three elements, so that the martensite content in the cast structure is more; the presence of a small amount of black network in the as-cast structure, which is distributed substantially along the grain boundaries, was judged to be due to the element segregation by considering that the metallographic structure is a structure which has not been heat-treated, but the element segregation is relatively light and can be eliminated by the subsequent heat treatment.
The density, specific heat, and thermal diffusivity of the casting in example 4 at each experimental temperature point were measured, respectively, and were determined according to the formula λ ═ α ρ C p (Note: α -thermal diffusivity, cm) 2 s -1 (ii) a Rho-density g.cm -3 ；C p -specific heat capacity J/(g · K); lambda-thermal conductivity W/(m.K)), meterThe thermal conductivity at each experimental temperature point was calculated and the results are shown in table 1.
TABLE 1 thermal conductivity (W/(m.K))
| Temperature (. degree.C.) | Casting piece |
| 25 | 32.158 |
| 100 | 33.879 |
| 200 | 35.48 |
| 300 | 36.716 |
| 400 | 37.127 |
| 500 | 36.272 |
As can be seen from table 1: in the temperature range of 25-100 ℃, the thermal conductivity of the die steel is far higher than that of H13 (22W/(m.K)) and also higher than that of 18Ni300 maraging steel. The thermal conductivity of the die steel at 400 ℃ is as high as 37.13W/(m.K).
FIG. 2 is a metallographic structure of the die steel aged at different aging temperatures for 4 hours in example 4, wherein a is 425 ℃, b is 450 ℃, c is 475 ℃, d is 500 ℃, e is 525 ℃, f is 550 ℃ and g is 575 ℃.
As can be seen from fig. 2: the structure after heat treatment is formed by mixing strip ferrite distributed in a network manner and massive martensite.
TABLE 2 Properties of 4h aged die steels at different aging temperatures
| Aging temperature (. degree.C.) | Hardness (HRC) | Tensile strength Ts (MPa) | Elongation El (%) |
| 425 | 29.10 | 927.32 | 13.42 |
| 450 | 33.53 | 991.91 | 14.15 |
| 475 | 34.27 | 989.77 | 13.13 |
| 500 | 33.83 | 986.74 | 14.99 |
| 525 | 35.67 | 948.44 | 16.35 |
| 550 | 31.23 | 917.87 | 16.44 |
| 575 | 28.50 | 765.34 | 15.17 |
As can be seen from Table 2, the hardness of the die steel is increased and then reduced along with the variation trend of the aging temperature, the hardness at the aging temperatures of 425 ℃ and 575 ℃ is obviously lower than that of the die steel treated by other aging temperatures, because the number of precipitates in the die steel after the aging treatment is relatively small when the aging temperature is lower, the hardening effect of the precipitates is not obvious, and the precipitated phase is still at high temperature after being completely precipitated when the aging temperature is higher, the phenomenon of polymerization and growth of the originally fine and dispersed precipitated phase occurs at this time, so that the hardening effect of the precipitated phase is weakened, and the hardness is reduced, so that the proper aging temperature interval of the die steel is 450-;
when the aging temperature is within the temperature range of 425-575 ℃, the tensile strength of the die steel shows the trend of increasing firstly and then decreasing along with the increase of the aging temperature. Obviously, the selection of the aging temperature at 475-; when the aging temperature is too high, the interface between the martensite laths disappears while the second phase aggregates to grow, so that the strength is obviously reduced and the martensite laths are in an overaging state;
the relationship between the elongation and the aging temperature is not obvious, the elongation generally has a trend of increasing with the increase of the aging temperature, and the increasing amplitude is smaller, which is probably because the higher the aging temperature is, the more thorough the elimination of the internal stress is, meanwhile, the dislocation density is reduced after the dislocation in the crystal grains slides and climbs, and the elongation shows a trend of increasing with the increase of the aging temperature under the combined action of multiple factors. The aging temperature is 475 ℃ and 525 ℃ in comprehensive consideration.
FIG. 3 is a metallographic structure of a die steel aged at 500 ℃ for different times in example 4, wherein the metallographic structure sequentially comprises solid solution + aging for 0h, solid solution + aging for 0.5h, solid solution + aging for 1h, and solid solution + aging for 4h from left to right.
As can be seen from fig. 3: after the die steel is subjected to heat treatment at 500 ℃ for different aging times, the structure of the die steel is a mixed structure of strip ferrite and strip martensite which are distributed in a network manner. After aging treatment at different aging times, the microstructure change can not be seen through a metallographic photograph, and the microstructure is not considered to be sensitive to the aging time during the aging treatment at 500 ℃.
TABLE 3500 ℃ ageing Properties of die steels at different times
| Heat treatment process | Hardness (HRC) | Tensile strength Ts (MPa) | Elongation El (%) |
| Solid solution and aging for 0h | 23.0 | 771 | 8.2 |
| Solid solution and aging for 0.5h | 32.4 | 930 | 11.8 |
| Solid solution and aging for 1h | 30.4 | 884 | 10.3 |
| Solid solution and aging for 2h | 33.1 | 966 | 13.2 |
| Solid solution and aging for 4h | 33.8 | 987 | 15.0 |
| Solid solution and aging for 8h | 34.3 | 998 | 13.8 |
As can be seen from table 3: the hardness of the die steel after solution treatment is only 23HRC, the hardness of the die steel is higher than that of the die steel after aging for 0.5h, the change trend of the hardness along with the aging time is wave-shaped, and the hardness is reduced and then increased, because a large amount of copper-rich phases are rapidly separated out when the aging time is 0.5h, the hardness of the material is improved, when the aging time is increased to 1h, not only are the separated phases continuously separated out to increase the hardness, but also dislocation rearrangement occurs to reduce the dislocation density in the material to reduce the hardness, and the comprehensive effect of the two determines the relationship between the hardness of the die steel after aging for 1h and the hardness of the die steel after aging for 0.5 h; after the aging time of the die steel reaches 4h, the aging time is continuously increased to 8h, the change of the hardness is small, and the influence of the aging time on the hardness relative to the aging temperature is small;
the elongation of the die steel after aging treatment is generally higher than that of the die steel after solution treatment, because the stress is released after the aging treatment, the dislocation density in the material is reduced, and the plasticity is improved; when the aging time is less than 4h, the strength of the die steel subjected to aging treatment is lower than the strength in a solid solution state, the strength of the die steel exceeds the strength in the solid solution state after the aging time reaches 4h, the reason that the aging strength is reduced in a short time is probably caused by reduction of dislocation density, and the material strength is increased because a precipitated phase is precipitated in sufficient time after the aging time reaches 4 h. The aging time is selected from 0.5-8h, preferably 2-8 h.
The experiment shows that the die steel has high heat conductivity and good toughness and strength.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art should be considered to be within the technical scope of the present invention, and the technical solutions and the inventive concepts thereof according to the present invention should be equivalent or changed within the scope of the present invention.
Claims (6)
1. The die steel with good toughness and high thermal conductivity is characterized by comprising the following components in percentage by weight: 0.04-0.06% of C, 0.7-0.8% of Ni, 1.4-1.6% of Cu, 0.65-0.75% of Mn, 0.35-0.45% of Si, 2.8-3.2% of Mo, 1.8-2.2% of W and the balance of Fe;
the preparation method of the die steel with good toughness and high thermal conductivity comprises the following steps:
s1, taking the raw materials, smelting and casting to obtain a casting with the same component ratio as the die steel with good toughness and high heat conductivity;
s2, carrying out solid solution treatment on the casting, quenching, and carrying out heat preservation and aging treatment at 475-.
2. The die steel with good toughness and high thermal conductivity as claimed in claim 1, wherein the die steel comprises the following components in percentage by weight: 0.05% of C, 0.75% of Ni, 1.5% of Cu, 0.7% of Mn, 0.4% of Si, 3% of Mo, 2% of W and the balance of Fe.
3. The die steel with good toughness and high thermal conductivity as claimed in claim 1 or 2, wherein in S2, the solid solution temperature is not less than 950 ℃, and the solid solution time is not less than 30 min.
4. The die steel with good toughness and high thermal conductivity as claimed in claim 1 or 2, wherein in S2, the heat preservation and aging treatment is carried out at 475-.
5. The die steel with good toughness and high thermal conductivity according to claim 1 or 2, wherein in S2, the die steel is quenched with water until the ingot casting temperature is room temperature.
6. The die steel with good toughness and high thermal conductivity as claimed in claim 1 or 2, wherein in S2, after aging, the die steel with good toughness and high thermal conductivity is obtained by air cooling to room temperature.
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| CN103774047A (en) * | 2012-10-20 | 2014-05-07 | 大同特殊钢株式会社 | Steel for molding die having excellent thermal conductivity, mirror polishing properties and toughness |
| CN111636037A (en) * | 2019-03-01 | 2020-09-08 | 育材堂（苏州）材料科技有限公司 | Hot work die steel, heat treatment method thereof and hot work die |
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2021
- 2021-12-31 CN CN202111673677.8A patent/CN114250422B/en active Active
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1174244A (en) * | 1996-03-01 | 1998-02-25 | 克罗索·洛利工业责任有限公司 | Steel usable especially for manufacture of moulds for injection moulding of plastic |
| JP2001152246A (en) * | 1999-11-22 | 2001-06-05 | Sanyo Special Steel Co Ltd | Method for producing steel for plastic molding die excellent in toughness, mirror finishing property and machinability |
| CN1511969A (en) * | 2002-11-06 | 2004-07-14 | 大同特殊钢株式会社 | Alloy tool steel and its producing method and mold using it |
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| CN101029373A (en) * | 2006-03-02 | 2007-09-05 | 日立金属株式会社 | Preharden steel with excellent cutting performance and toughness and manufacturing method therefor |
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| CN103282530A (en) * | 2010-12-27 | 2013-09-04 | 日立金属株式会社 | Die steel having superior rusting resistance and thermal conductivity, and method for producing same |
| CN103774047A (en) * | 2012-10-20 | 2014-05-07 | 大同特殊钢株式会社 | Steel for molding die having excellent thermal conductivity, mirror polishing properties and toughness |
| CN111636037A (en) * | 2019-03-01 | 2020-09-08 | 育材堂（苏州）材料科技有限公司 | Hot work die steel, heat treatment method thereof and hot work die |
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| CN114250422A (en) | 2022-03-29 |
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