CN106811580B - A kind of annealing process of H13 hot die steels - Google Patents
A kind of annealing process of H13 hot die steels Download PDFInfo
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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
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
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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
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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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
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- 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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- 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
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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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- Crystallography & Structural Chemistry (AREA)
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Abstract
A kind of annealing process of H13 hot die steels, belongs to mold steel heat treatment process field.Technique includes：(1) H13 steel blanks are cooled to 400~500 DEG C after forging, it is fitted into stove, it is warming up to 720~750 DEG C of preheating insulations with the heating rate of 25~80 DEG C/h, 1 2h of soaking time, again 980 1050 DEG C are warming up to the heating rate of 25~80 DEG C/h, furnace charge keeps the temperature 3 5h again after protecting thoroughly, is then furnace-cooled to≤550 DEG C and air-cooled comes out of the stove；Hot charging stove is warming up to 900 950 DEG C with the heating rate of 25~80 DEG C/h, and furnace charge keeps the temperature 0.5 1h after protecting thoroughly, air-cooled to come out of the stove, and completes preprocessing process；300 400 DEG C of shove charges, are warming up to 880 DEG C ± 10 DEG C with the heating rate of 25~80 DEG C/h, keep the temperature 4 6h, are cooled to 760 DEG C ± 10 DEG C with the cooling velocity of 15 20 DEG C/h, after keeping the temperature 8 12h, are cooled to≤500 DEG C with the cooling velocity of 15 20 DEG C/h and air-cooled come out of the stove.The advantage is that tissue in distribution of carbides uniformity, thinning microstructure, eliminate original structure in net carbide the defects of, reduce annealing hardness.
Description
Technical field
The invention belongs to mold steel heat treatment process field, more particularly to a kind of spheroidizing work of H13 hot die steels
Skill.Improved-type annealing suitable for H13 steel forgings after annealing and unqualified annealed structure.
Background technology
H13 steel is current most widely used hot die steel, and such steel is usually applied to rapid heat cycle and high temperature and pressure
Environment, most important failure mode are heat fatigue cracking, coarse crackle, plastic deformation, abrasion etc., and wherein heat fatigue cracking is
Influence the most important failure mode in hot-work die service life.It is generally believed that intensity and temper resistance are to influence thermal fatigue resistance
Main factor, and high impact flexibility is conducive to the relaxation of local stress, prevents crack propagation.Intensity and plasticity are tired to heat
The different phase of labor may have different influences.The germinating stage of heat fatigue cracking is mainly by strength control, and extension phase master
It to be controlled by toughness plasticity, when hot tearing occurs, the higher toughness of steel can prevent the extension of crackle, prevent from being formed through mould
The big crackle of tool.Therefore, high intensity and good toughness plasticity contribute the thermal fatigue resistance of hot forming dies materials.Production
In can by suitably quenching, tempering process obtain needed for intensity, but raisings of toughness need raising steel quality.
Obtain the necessary condition that good annealed structure is H13 steel high tenacity.For H13 steel, by normal technique
After forging is cooling, martensite, Martensite-Bainite Mixed Microstructure can be obtained, hardness is higher, reaches 50HRC or so, it is difficult to machining.Separately
Outside, forging process also generates harmful effect to tissue, as grain size distribution is uneven and is made slowly excessively by cooling after forged speed
At carbide Intergranular precipitation the defects of.It needs to eliminate the residual stress in steel by spheroidizing, reduces hardness, makes alloy carbon
Compound is uniformly distributed, at the same also be finally quench, tempering heat treatment performs structural preparation.Therefore, spheroidizing is in H13 steel
It is extremely important in production process.
The quality of annealed structure is the important judgment basis of preliminary assessment H13 steel quality grades.NADCA 207-2003 marks
Clear stipulaties need to grade to annealed structure in standard, and have formulated detailed grading collection of illustrative plates.It is analysed in H13 steel annealing processes
The scale particle size of the alloy carbide gone out, distribution are restricted by various factors.For H13 steel, existing annealing process technology be
It directly anneals to steel billet after cooling after forged to certain temperature, technique is generally basede on the critical point of H13 steel, is held according to isothermal annealing
Row, technique are：860-890 DEG C of austenitizing, control are cooled at a slow speed 740-780 DEG C of isothermal, and control is cooled at a slow speed temperature≤500 DEG C
It is air-cooled to come out of the stove.The technique is used by most of manufacturers.But it finds in practice, the group of the direct spheroidizing of steel billet after finish-forging
The requirement of NADCA 207#-2003 cannot be met by knitting.It is mainly manifested in net carbide, chain-like carbide and distribution of carbides
Uneven etc., netted and chain-like carbide usually can be genetic to steel belt roof bolt state, be caused to the transverse impact toughness of steel
Large effect.So that spheroidizing rank is relatively low when H13 steel annealed states are dispatched from the factory, quality is also poor.The main reason is that
The tissue before isothermal annealing is not pre-processed, tissue is kept down after non-uniform forging.In recent years, it was moved back for H13 steel
Normalizing procedure is added on the basis of traditional isothermal annealing in the problem of fire tissue difference, researcher, and normalizing temperature is generally 1000-
1100 DEG C, though the H13 steel annealed structures after normalizing have improvement, carbide size is excessively tiny, and hardness is higher, carbide
Distribution still has certain orientation, and nodularization effect fails the super quality level for reaching NADCA 207-2003 standards.
Invention content
The object of the present invention is to provide a kind of annealing process of H13 hot die steels, overcome existing technology and lack
It falls into, which can improve distribution of carbides uniformity in the annealed structure of H13 steel, and thinning microstructure is eliminated in original structure
The defects of net carbide, reduces annealing hardness.The technique can also be applied to improve underproof annealed structure simultaneously.
To achieve the above object, the annealing heat-treats method of H13 steel according to the present invention, including following steps：
(1) H13 steel blanks are cooled to 400~500 DEG C after forging, and are fitted into stove, are heated up with the heating rate of 25~80 DEG C/h
To 720~750 DEG C of preheating insulations, soaking time 1-2h, then it is warming up to 980-1050 DEG C with the heating rate of 25~80 DEG C/h, stove
Material keeps the temperature 3-5h again after protecting thoroughly, is then furnace-cooled to≤550 DEG C and air-cooled comes out of the stove；
(2) hot charging stove is warming up to 900-950 DEG C with the heating rate of 25~80 DEG C/h, and furnace charge keeps the temperature 0.5-1h after protecting thoroughly,
It is air-cooled to come out of the stove, complete preprocessing process；
(3) 300-400 DEG C of shove charge is warming up to 880 DEG C ± 10 DEG C with the heating rate of 25~80 DEG C/h, keeps the temperature 4-6h, with
The cooling velocity of 15-20 DEG C/h is cooled to 760 DEG C ± 10 DEG C, after keeping the temperature 8-12h, is cooled to≤500 with the cooling velocity of 15-20 DEG C/h
It is DEG C air-cooled to come out of the stove.
The body chemical component weight % of the hot die steel is as follows：Carbon C:0.37~0.42%, silicon Si:0.80~
1.20%, sulphur S≤0.006%, phosphorus P≤0.01%, manganese Mn:0.20~0.5%, molybdenum Mo:1.20~1.75%, chromium Cr:5.00
~5.50%, vanadium V:0.80~1.20%, remaining is Fe and inevitable impurity.
Compared with prior art, the beneficial effects of the invention are as follows
1,750 DEG C of preheating insulations are warming up to the heating rate of≤80 DEG C/h, soaking time 1h avoids heating rate too fast
Cause steel crackle.980-1050 DEG C of furnace charge keeps the temperature 3-5h after protecting thoroughly, for the homogenization and carbide dissolution process of tissue, H13
In the temperature long period grain coarsening phenomenon do not occur for steel, while making chain in original structure, netted carbonization
Object dissolves, and retains a part of undissolved carbide.The type of cooling selection furnace cooling be unlikely to so that blank in cooling procedure due to
Internal stress cracks, while furnace cooling to be partly dissolved into the alloy carbide of matrix and is precipitated again.
2,900-950 DEG C, furnace charge keeps the temperature 0.5-1h after protecting thoroughly, air-cooled to come out of the stove as cryogenic normalizing process, and the process is further
The a small amount of netted and chain-like carbide that is formed in aforementioned process is eliminated, while being retained to greatest extent by being formed during previous
A large amount of equally distributed alloy carbide particles.Cryogenic normalizing tissue has more undissolved carbide particles, while having
Even martensitic structure also reduces and uses structural stress caused by high temperature normalizing technique.
3, after above-mentioned homogenization and cryogenic normalizing pretreatment, it can be obtained carbonization using traditional isothermal annealed processes
Object Dispersed precipitate, particle size are moderate, eliminate netted and chain-like carbide homo genizing annelaing tissue, and lower annealing hardness is non-
Often be conducive to subsequent machining.
4, compared with directly annealing after tradition is forged, H13 steel transverse impact toughness can be improved using present invention process.
Description of the drawings
Fig. 1 is that the annealing metallographic structure after isothermal annealing is directly used after forging.
Fig. 2 is that pretreating process using the present invention carries out the annealing metallographic structure after isothermal annealing again.
Fig. 3 is the annealing SEM tissues after directly using isothermal annealing after forging.
Fig. 4 is that pretreating process using the present invention carries out the annealing SEM tissues after isothermal annealing again.
Specific implementation mode
Embodiment 1
Select sectional dimension after forgingPole, specific heat treatment process are as follows：
(1) after forgingSteel blank is cooled to 430 DEG C, is fitted into stove, is warming up to the heating rate of 70 DEG C/h
The heating rate of 750 DEG C of preheating insulations, soaking time 1h, then 70 DEG C/h are warming up to 1000 DEG C, and furnace charge keeps the temperature 3h again after protecting thoroughly, with
After be furnace-cooled to 500 DEG C and air-cooled come out of the stove.
(2) hot charging stove is warming up to 900 DEG C with the heating rate of 70 DEG C/h, and furnace charge keeps the temperature 0.5h after protecting thoroughly, air-cooled to come out of the stove,
Complete preprocessing process.
Blank (control sample) and the pretreated blank of completion after (3) 300 DEG C of shove charges, including forging, with the heating of 70 DEG C/h
Speed is warming up to 880 DEG C, keeps the temperature 4h, is cooled to 760 DEG C with the cooling velocity of 15 DEG C/h, after keeping the temperature 8h, with the cooling speed of 15 DEG C/h
Degree be cooled to 455 DEG C it is air-cooled come out of the stove, complete entire heat treatment process.
It is sampled by H13 round bar center portions, specimen size is 15 × 15 × 20mm, and structure observation direction is laterally, using 4%
Specimen surface after nitric acid alcohol etch polishing, annealing metallographic structure is as shown in Fig. 2, SEM tissues are as shown in Figure 4.With it is straight after forging
The tissue for connecing annealing is compared (see Fig. 1 and Fig. 4), and carbide dispersion degree and particle size distribution are enhanced, and base
Originally netted and chain-like carbide is eliminated；Annealing hardness also drops to 183HB by 215HB, with obvious effects.By 1030 DEG C × 30min
The heat treatment process adjustment impact specimen hardness of+600 DEG C of oil quenchinng × 2h air-cooled tempering twice is 44-46HRC, measurement standard
Charpy v-notch (10 × 10 × 55mm) impact value, direct isothermal annealing is 9.8J after forging, by pretreatment+isothermal of the present invention
Annealing process is 11.1J, improves 13.2%.
Embodiment 2
Select sectional dimension after forgingPole, specific heat treatment process are as follows：
(1) after forgingSteel blank is cooled to 480 DEG C, is fitted into stove, is warming up to the heating rate of 70 DEG C/h
The heating rate of 750 DEG C of preheating insulations, soaking time 1h, then 70 DEG C/h are warming up to 980 DEG C, and furnace charge keeps the temperature 5h again after protecting thoroughly, with
After be furnace-cooled to 480 DEG C and air-cooled come out of the stove.
(2) hot charging stove is warming up to 900 DEG C with the heating rate of 70 DEG C/h, and furnace charge keeps the temperature 1h after protecting thoroughly, air-cooled to come out of the stove, complete
At preprocessing process.
Blank (control sample) and the pretreated blank of completion after (3) 370 DEG C of shove charges, including forging, with the heating of 70 DEG C/h
Speed is warming up to 880 DEG C, keeps the temperature 6h, is cooled to 760 DEG C with the cooling velocity of 15 DEG C/h, after keeping the temperature 10h, with the cooling speed of 20 DEG C/h
Degree be cooled to 500 DEG C it is air-cooled come out of the stove, complete entire heat treatment process.
It is sampled by H13 round bar center portions, specimen size is 15 × 15 × 20mm, and structure observation direction is laterally, using 4%
Specimen surface after nitric acid alcohol etch polishing, the sample carbide dispersion degree by pretreatment+spheroidizing and particle ruler
Very little distribution is enhanced, and also essentially eliminates netted and chain-like carbide；Annealing hardness also drops to 189HB by 221HB,
It is with obvious effects.By the heat treatment process adjustment impact examination of+600 DEG C × 2h of 1030 DEG C × 30min oil quenchinngs air-cooled tempering twice
Sample hardness is 44-46HRC, and measurement standard Charpy v-notch (10 × 10 × 55mm) impact value, direct isothermal annealing is after forging
9.6J is 10.6J by pretreatment+isothermal annealed processes of the present invention, improves 10.4%.
Claims (1)
1. a kind of annealing process of H13 hot die steels, which is characterized in that annealing process includes the following steps：
(1) H13 steel blanks are cooled to 400~500 DEG C after forging, and are fitted into stove, 720 are warming up to the heating rate of 25~80 DEG C/h
~750 DEG C of preheating insulations, soaking time 1-2h, then it is warming up to 980-1050 DEG C with the heating rate of 25~80 DEG C/h, furnace charge is saturating
3-5h is kept the temperature after guarantor again ,≤550 DEG C is then furnace-cooled to and air-cooled comes out of the stove；
(2) hot charging stove is warming up to 900-950 DEG C with the heating rate of 25~80 DEG C/h, and furnace charge keeps the temperature 0.5-1h after protecting thoroughly, air-cooled
It comes out of the stove, completes preprocessing process；
(3) 300-400 DEG C of shove charge is warming up to 880 DEG C ± 10 DEG C with the heating rate of 25~80 DEG C/h, 4-6h is kept the temperature, with 15-20
DEG C/cooling velocity of h is cooled to 760 DEG C ± 10 DEG C, after keeping the temperature 8-12h ,≤500 DEG C of skies are cooled to the cooling velocity of 15-20 DEG C/h
It is cold to come out of the stove；
The body chemical component weight % of the hot die steel is as follows：Carbon C:0.37~0.42%, silicon Si:0.80~
1.20%, sulphur S≤0.006%, phosphorus P≤0.01%, manganese Mn:0.20~0.5%, molybdenum Mo:1.20~1.75%, chromium Cr:5.00
~5.50%, vanadium V:0.80~1.20%, remaining is Fe and inevitable impurity.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN108823381B (en) * | 2018-07-12 | 2020-04-07 | 河钢股份有限公司 | Heat treatment process for improving structure uniformity of H13 hot work die steel forging material |
| CN109182680B (en) * | 2018-11-19 | 2020-06-16 | 攀钢集团江油长城特殊钢有限公司 | Method for controlling annealing hardness of martensitic stainless steel rod wire for cold heading |
| CN110317934B (en) * | 2019-06-20 | 2021-08-24 | 河钢股份有限公司 | Heat treatment process for improving uniformity of H13 steel annealing structure |
| CN111455149A (en) * | 2020-05-11 | 2020-07-28 | 山东邦巨实业有限公司 | Isothermal spheroidizing annealing process for H13 steel |
| CN111733312B (en) * | 2020-08-12 | 2021-06-22 | 燕山大学 | Heat treatment process for improving comprehensive mechanical property of H13 steel |
| CN113151641B (en) * | 2021-04-21 | 2022-04-29 | 中山市江润金属压铸有限公司 | Mold activation method capable of prolonging service life of mold |
| CN113337780A (en) * | 2021-05-31 | 2021-09-03 | 浙江协力机械工具有限公司 | Die steel and preparation method thereof |
| CN114941061B (en) * | 2022-05-16 | 2024-04-19 | 洛阳中重铸锻有限责任公司 | Heat treatment method for super-thick section hot work die steel forging |
| CN116987846B (en) * | 2023-09-04 | 2024-05-17 | 中国机械总院集团北京机电研究所有限公司 | Method for improving impact toughness of hot work die steel annealing structure |
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| CN1234883C (en) * | 2003-11-01 | 2006-01-04 | 湖南科技大学 | Isothermal spheroidizing technique for H13 steel |
| CN102212756A (en) * | 2011-05-04 | 2011-10-12 | 上海大学 | Chromium-molybdenum-vanadium hotwork tool-die steel and heat treatment process thereof |
| CN103333997B (en) * | 2013-07-02 | 2014-12-10 | 武汉钢铁(集团)公司 | Annealing heat treatment method of H13 die steel |
| CN105695703A (en) * | 2014-11-28 | 2016-06-22 | 重庆基石机械有限公司 | Heat treatment process for die steel |
| CN105734231A (en) * | 2014-12-09 | 2016-07-06 | 重庆金国凯畅机床厂 | Heat treatment process for H13 steel |
| CN104726659B (en) * | 2015-02-10 | 2017-02-01 | 中原特钢股份有限公司 | Thermal treatment process for improving microscopic coarse grains and microstructures of H13 forged piece |
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