CN110317934A - Improve the heat treatment process of H13 steel annealed structure uniformity - Google Patents
Improve the heat treatment process of H13 steel annealed structure uniformity Download PDFInfo
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- CN110317934A CN110317934A CN201910536450.5A CN201910536450A CN110317934A CN 110317934 A CN110317934 A CN 110317934A CN 201910536450 A CN201910536450 A CN 201910536450A CN 110317934 A CN110317934 A CN 110317934A
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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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Abstract
The invention discloses a kind of heat treatment process for improving H13 steel annealed structure uniformity, technical process are as follows: (1) the H13 steel after forging is cooled to 400~500 DEG C, is packed into heating furnace, 680~750 DEG C of heating temperature, 2~4h of heat preservation are come out of the stove air-cooled；(2) hot charging furnace after the H13 steel is air-cooled to 300~400 DEG C is warming up to 800~850 DEG C of preheating insulations, 2~4h of soaking time with the heating rate of 50~120 DEG C/h；1060~1100 DEG C are warming up to the heating rate of 50~120 DEG C/h again, furnace charge keeps the temperature 1~2h after protecting thoroughly；It comes out of the stove and is air-cooled to≤100 DEG C；(3) H13 steel is packed into heating furnace, is warming up to 860~900 DEG C, 4~6h of heat preservation；It is subsequently cooled to 720~740 DEG C, 6~8h of heat preservation；It is warming up to 840~880 DEG C, 4~6h of heat preservation again；It is cooled to 720~740 DEG C, 6~8h of heat preservation；≤ 500 DEG C are finally cooled to, is come out of the stove air-cooled.This technique avoids carbide along crystal boundary in chainlike distribution, significantly improves anneal of material structural homogenity and equal orientation performance.
Description
Technical field
The present invention relates to a kind of mold steel heat treatment process, especially a kind of heat for improving H13 steel annealed structure uniformity
Treatment process.
Background technique
H13 steel heat resistance with higher, higher toughness, excellent thermal fatigue resistance and erosion performance are extensive
Applied to hot-forging die, aluminium alloy casting die and hot extruding die.During military service, die cavity is subjected to repeatedly H13 steel hot-work die
Heating and cooling, while the effect that also has certain impact, common main failure forms are heat fatigue cracking, die cavity heat etching
Abrasion and die cavity plastic deformation, wherein heat fatigue cracking is to cause the main reason of H13 hot-work die initial failure.Heat fatigue is split
The germinating stage of line is mainly by strength control, and extension phase is mainly controlled by toughness, therefore, high temperature strength and toughness it is good
Good cooperation is most important to H13 steel anti-fatigue performance is improved.
Uniform annealed structure is to guarantee the important prerequisite of H13 steel high-strength tenacity.Tissue is martensite, shellfish after H13 steel forging
The line and staff control of family name's body and pearlite, and hardness is higher, usually needs to make annealing treatment before delivery, to reduce material hardness and be
Subsequent heat treatment carries out tissue preparation.H13 routine isothermal annealed processes are as follows: 860~890 DEG C of austenitizings, it is furnace-cooled to 700~
After 760 DEG C of isothermal spheroidizings, be furnace-cooled to≤500 DEG C come out of the stove it is air-cooled.After being made annealing treatment by above-mentioned method for annealing to H13 steel, move back
It is in chainlike distribution that there are carbide along crystal boundary in fire tissue, compares annealed structure judge picture in NADCA#207-2003 and is determined as
AS16 grades, belong to unqualified rank.This chain-like carbide, which can be inherited, to be quenched, in tempered structure, equal to the intensity and toughness of material
There are larger impact, especially reduction transverse impact toughness.Chain-like carbide and net carbide are how eliminated, obtains carbide more
Distribution is dissipated, of uniform size moderate, the high annealed structure of granule roundness is the weight for improving H13 steel quality level and die life
Want means.
Summary of the invention
The technical problem to be solved in the present invention is to provide it is a kind of improve H13 steel annealed structure uniformity heat treatment process,
To improve H13 steel quality level and die life.
In order to solve the above technical problems, the technical solution used in the present invention is: the H13 steel after forging is cooled to by (1)
400~500 DEG C, it is packed into heating furnace, 680~750 DEG C of heating temperature, 2~4h of heat preservation are come out of the stove air-cooled；
(2) hot charging furnace after the H13 steel of step (1) processing is air-cooled to 300~400 DEG C, with the heating rate of 50~120 DEG C/h
It is warming up to 800~850 DEG C of preheating insulations, 2~4h of soaking time；1060 are warming up to again with the heating rate of 50~120 DEG C/h~
1100 DEG C, furnace charge keeps the temperature 1~2h after protecting thoroughly；It comes out of the stove and is air-cooled to≤100 DEG C；
(3) the H13 steel by step (2) processing is packed into heating furnace, is warming up to 860~900 with the heating rate of 50~120 DEG C/h
DEG C, heat preservation 4~6h；Then 720~740 DEG C, 6~8h of heat preservation are cooled to the cooling rate of 20~50 DEG C/h；Again with 50~120
DEG C/heating rate of h is warming up to 840~880 DEG C, 4~6h of heat preservation；720 are cooled to again with the cooling rate of 20~50 DEG C/h~
740 DEG C, 6~8h of heat preservation；≤ 500 DEG C finally are cooled to the cooling rate of 20~50 DEG C/h, is come out of the stove air-cooled.
The chemical component of H13 steel of the present invention forms and its mass percentage are as follows: C 0.38~0.43%, Si 0.80
~1.20%, Mn 0.30~0.50%, Cr 5.10~5.60%, Mo 1.30~1.60%, V 0.80~1.20%, P≤0.020%,
S≤0.003%, O≤0.005%, N≤0.015%, remaining is Fe and inevitable impurity.
The sectional dimension of H13 steel after forging of the present invention is 90~170mm of φ.
The beneficial effects of adopting the technical scheme are that the H13 steel after forging is cooled to 350 by the 1, present invention
~500 DEG C, it is packed into heating furnace, 680~750 DEG C of heating temperature, 2~4h is kept the temperature, comes out of the stove air-cooled；It effectively eliminates in material and answers
Power, avoid in cooling procedure as forging stock internal-external temperature difference it is excessive caused by material cracks.2, forging stock hot charging furnace of the present invention, with 50
The heating rate of~120 DEG C/h is warming up to 1050~1100 DEG C, and furnace charge keeps the temperature 1~2h after protecting thoroughly again, is air-cooled to room temperature；The process
It is precipitated again by the abundant back dissolving of carbide, distribution of carbides uniformity can be improved, obtain uniformly tiny single cryptocrystalline martensite
Tissue carries out tissue preparation for subsequent spheroidizing.3, pretreated H13 steel is packed into heating furnace by the present invention, makes H13 steel
In carbide a nodularization of 4~6h and 720~740 DEG C of 6~8h of heat preservation is kept the temperature continuously across 860~900 DEG C, with 840~
The secondary nodularization of 880 DEG C of heat preservations, 4~6h and 720~740 DEG C of 6~8h of heat preservation；Carbide particle roundness is effectively increased, greatly
Reduce the quantity of large-size carbon compound and little particle carbide, obtains carbide dispersion distribution, moderate, particle circle of uniform size
The high annealed structure of whole degree.4, the present invention is sampled in annealed state H13 steel core portion, is processed into compared with the processing of conventional isothermal annealing
10mm × 10mm × 55mm v-shaped notch Charpy bar, annealing side knock function be >=55J, transverse and longitudinal impact work ratio >=
0.85, annealing hardness≤182HB, annealed structure rank reaches AS3 level above in NADCA#207-2003 standard.The present invention can
Carbide dispersion distribution is obtained, of uniform size moderate, the high H13 steel annealed structure of granule roundness avoids carbide along brilliant
Boundary is in chainlike distribution, significantly improves anneal of material structural homogenity and equal orientation performance.
Detailed description of the invention
The present invention will be further described in detail below with reference to the accompanying drawings and specific embodiments.
Fig. 1 is the H13 steel metallographic structure figure after the embodiment of the present invention 1 makes annealing treatment；
Fig. 2 is conventional spheroidizing treated H13 steel metallographic structure figure；
Fig. 3 is the H13 steel SEM figure after the embodiment of the present invention 1 makes annealing treatment；
Fig. 4 is conventional spheroidizing treated H13 steel SEM figure.
Specific embodiment
Embodiment 1: the heat treatment process of this raising H13 steel annealed structure uniformity is described in detail below.
(1) the H13 steel bar of φ 130mm after forging is cooled to 450 DEG C, is packed into heating furnace, 720 DEG C of heating temperature is protected
Warm 3h comes out of the stove air-cooled.
(2) hot charging furnace after the H13 steel is air-cooled to 350 DEG C is warming up to 825 DEG C of preheatings with the heating rate of 70 DEG C/h and protects
Temperature, soaking time 3h；It is warming up to 1080 DEG C for the second time with the heating rate of 100 DEG C/h again, furnace charge keeps the temperature 1h after protecting thoroughly again, comes out of the stove
It is air-cooled to room temperature, completes preprocessing process.
(3) H13 steel is packed into heating furnace, 880 DEG C, heat preservation 5h is warming up to the heating rate of 85 DEG C/h；With 35 DEG C/h's
Cooling rate is cooled to 730 DEG C, heat preservation 7h；It is warming up to 870 DEG C for the second time with the heating rate of 85 DEG C/h again, keeps the temperature 5h；With 35
DEG C/cooling rate of h is cooled to 730 DEG C, heat preservation 7h for the second time；Finally 485 are cooled to the cooling rate third time of 35 DEG C/h
DEG C, it comes out of the stove air-cooled.
The chemical component of H13 steel described in the present embodiment is shown in Table 1；H13 steel after heat treatment is sampled by bar center portion, detection
Method standard refers to GB/T229-2007, after corroding after Mechanical polishing using 4% nitric acid alcohol, observes horizontal organization, metallographic
Tissue is as shown in Figure 1, SEM tissue is as shown in Figure 3；Compared with the tissue (see Fig. 2 and Fig. 4) after conventional isothermal annealing, carbide
Disperse degree, dimensional homogeneity and granule roundness are improved largely, and completely eliminate carbide along brilliant chainlike distribution, annealing
Tissue rank reaches the level of the AS3 in NADCA#207-2003 standard；Annealing hardness drops to 182HB by 212HB, and annealing is laterally
Ballistic work is increased to 57J by 39J, and transverse and longitudinal impacts work ratio and is increased to 0.85 by 0.46.
Embodiment 2: the heat treatment process of this raising H13 steel annealed structure uniformity is described in detail below.
(1) the H13 steel bar of φ 90mm after forging is cooled to 400 DEG C, is packed into heating furnace, 680 DEG C of heating temperature, heat preservation
2h comes out of the stove air-cooled.
(2) hot charging furnace after the H13 steel is air-cooled to 300 DEG C is warming up to 800 DEG C of preheatings with the heating rate of 90 DEG C/h and protects
Temperature, soaking time 4h；It is warming up to 1060 DEG C for the second time with the heating rate of 120 DEG C/h again, furnace charge keeps the temperature 2h after protecting thoroughly again, comes out of the stove
It is air-cooled to room temperature, completes preprocessing process.
(3) H13 steel is packed into heating furnace, 860 DEG C, heat preservation 6h is warming up to the heating rate of 120 DEG C/h；With 50 DEG C/h's
Cooling rate is cooled to 720 DEG C, heat preservation 8h；840 DEG C, heat preservation 6h are warming up to for the second time with the heating rate of 120 DEG C/h again；With 50
DEG C/cooling rate of h is cooled to 720 DEG C, heat preservation 8h for the second time；Finally 460 are cooled to the cooling rate third time of 50 DEG C/h
DEG C, it comes out of the stove air-cooled.
The chemical component of H13 steel described in the present embodiment is shown in Table 1；H13 steel after heat treatment is sampled by bar center portion, through machine
After corroding after tool grinding and polishing using 4% nitric acid alcohol, horizontal organization, carbide dispersion degree, dimensional homogeneity in annealed structure are observed
And granule roundness improves a lot, structural homogenity is good；Annealing hardness drops to 180HB by 209HB, laterally punching of annealing
It hits function and 58.5J is increased to by 41J, transverse and longitudinal impacts work ratio and is increased to 0.92 by 0.51.
Embodiment 3: the heat treatment process of this raising H13 steel annealed structure uniformity is described in detail below.
(1) the H13 steel bar of φ 170mm after forging is cooled to 500 DEG C, is packed into heating furnace, 750 DEG C of heating temperature is protected
Warm 4h comes out of the stove air-cooled.
(2) hot charging furnace after the H13 steel is air-cooled to 400 DEG C is warming up to 850 DEG C of preheatings with the heating rate of 50 DEG C/h and protects
Temperature, soaking time 2h；It is warming up to 1100 DEG C for the second time with the heating rate of 80 DEG C/h again, furnace charge keeps the temperature 2h again after protecting thoroughly, empty out
It is cooled to room temperature, completes preprocessing process.
(3) H13 steel is packed into heating furnace, 900 DEG C, heat preservation 4h is warming up to the heating rate of 50 DEG C/h；With 20 DEG C/h's
Cooling rate is cooled to 740 DEG C, heat preservation 6h；880 DEG C, heat preservation 4h are warming up to for the second time with the heating rate of 50 DEG C/h again；With 20
DEG C/cooling rate of h is cooled to 740 DEG C, heat preservation 6h for the second time；Finally 490 are cooled to the cooling rate third time of 20 DEG C/h
DEG C, it comes out of the stove air-cooled.
The chemical component of H13 steel described in the present embodiment is shown in Table 1；H13 steel after heat treatment is sampled by bar center portion, through machine
After corroding after tool grinding and polishing using 4% nitric acid alcohol, horizontal organization, carbide dispersion degree, dimensional homogeneity in annealed structure are observed
And granule roundness improves a lot, structural homogenity is good；Annealing hardness drops to 180HB by 213HB, laterally punching of annealing
It hits function and 55J is increased to by 43.5J, transverse and longitudinal impacts work ratio and is increased to 0.87 by 0.42.
Embodiment 4: the heat treatment process of this raising H13 steel annealed structure uniformity is described in detail below.
(1) the H13 steel bar of φ 110mm after forging is cooled to 420 DEG C, is packed into heating furnace, 700 DEG C of heating temperature is protected
Warm 2.5h comes out of the stove air-cooled.
(2) hot charging furnace after the H13 steel is air-cooled to 320 DEG C is warming up to 810 DEG C of preheatings with the heating rate of 80 DEG C/h and protects
Temperature, soaking time 3.5h；It is warming up to 1070 DEG C for the second time with the heating rate of 110 DEG C/h again, furnace charge keeps the temperature 1.5h after protecting thoroughly again,
It comes out of the stove and is air-cooled to 100 DEG C, complete preprocessing process.
(3) H13 steel is packed into heating furnace, 870 DEG C, heat preservation 5.5h is warming up to the heating rate of 70 DEG C/h；With 30 DEG C/h
Cooling rate be cooled to 725 DEG C, heat preservation 7.5h；850 DEG C, heat preservation are warming up to for the second time with the heating rate of 70 DEG C/h again
5.5h；It is cooled to 725 DEG C, heat preservation 7.5h for the second time with the cooling rate of 30 DEG C/h；Finally with the cooling rate third of 30 DEG C/h
It is secondary to be cooled to 450 DEG C, it comes out of the stove air-cooled.
The chemical component of H13 steel described in the present embodiment is shown in Table 1；H13 steel after heat treatment is sampled by bar center portion, through machine
After corroding after tool grinding and polishing using 4% nitric acid alcohol, horizontal organization, carbide dispersion degree, dimensional homogeneity in annealed structure are observed
And granule roundness improves a lot, structural homogenity is good；Annealing hardness drops to 181HB by 210HB, laterally punching of annealing
It hits function and 57J is increased to by 40.5J, transverse and longitudinal impacts work ratio and is increased to 0.90 by 0.49.
Embodiment 5: the heat treatment process of this raising H13 steel annealed structure uniformity is described in detail below.
(1) the H13 steel bar of φ 150mm after forging is cooled to 470 DEG C, is packed into heating furnace, 740 DEG C of heating temperature is protected
Warm 3.5h comes out of the stove air-cooled.
(2) hot charging furnace after the H13 steel is air-cooled to 380 DEG C is warming up to 830 DEG C of preheatings with the heating rate of 120 DEG C/h and protects
Temperature, soaking time 2.5h；It is warming up to 1090 DEG C for the second time with the heating rate of 50 DEG C/h again, furnace charge keeps the temperature 1.5h after protecting thoroughly again,
It is air-cooled to 50 DEG C out, completes preprocessing process.
(3) H13 steel is packed into heating furnace, 890 DEG C, heat preservation 4.5h is warming up to the heating rate of 100 DEG C/h；With 40 DEG C/h
Cooling rate be cooled to 735 DEG C, heat preservation 6.5h；860 DEG C, heat preservation are warming up to for the second time with the heating rate of 100 DEG C/h again
4.5h；It is cooled to 735 DEG C, heat preservation 6.5h for the second time with the cooling rate of 40 DEG C/h；Finally with the cooling rate third of 40 DEG C/h
It is secondary to be cooled to 500 DEG C, it comes out of the stove air-cooled.
The chemical component of H13 steel described in the present embodiment is shown in Table 1；H13 steel after heat treatment is sampled by bar center portion, through machine
After corroding after tool grinding and polishing using 4% nitric acid alcohol, horizontal organization, carbide dispersion degree, dimensional homogeneity in annealed structure are observed
And granule roundness improves a lot, structural homogenity is good；Annealing hardness drops to 181HB by 212HB, laterally punching of annealing
It hits function and 56.5J is increased to by 41J, transverse and longitudinal impacts work ratio and is increased to 0.86 by 0.48.
Table 1: the chemical component (wt.%) of H13 steel described in each embodiment
In table 1, surplus is Fe and inevitable impurity.
Claims (3)
1. a kind of heat treatment process for improving H13 steel annealed structure uniformity, which is characterized in that its technical process are as follows: (1) will forging
H13 steel after making is cooled to 400~500 DEG C, is packed into heating furnace, and 680~750 DEG C of heating temperature, 2~4h of heat preservation are come out of the stove air-cooled；
(2) hot charging furnace after the H13 steel of step (1) processing is air-cooled to 300~400 DEG C, with the heating rate of 50~120 DEG C/h
It is warming up to 800~850 DEG C of preheating insulations, 2~4h of soaking time；1060 are warming up to again with the heating rate of 50~120 DEG C/h~
1100 DEG C, furnace charge keeps the temperature 1~2h after protecting thoroughly；It comes out of the stove and is air-cooled to≤100 DEG C；
(3) the H13 steel by step (2) processing is packed into heating furnace, is warming up to 860~900 with the heating rate of 50~120 DEG C/h
DEG C, heat preservation 4~6h；Then 720~740 DEG C, 6~8h of heat preservation are cooled to the cooling rate of 20~50 DEG C/h；Again with 50~120
DEG C/heating rate of h is warming up to 840~880 DEG C, 4~6h of heat preservation；720 are cooled to again with the cooling rate of 20~50 DEG C/h~
740 DEG C, 6~8h of heat preservation；≤ 500 DEG C finally are cooled to the cooling rate of 20~50 DEG C/h, is come out of the stove air-cooled.
2. the heat treatment process according to claim 1 for improving H13 steel annealed structure uniformity, which is characterized in that described
The chemical component of H13 steel forms and its mass percentage are as follows: and C 0.38~0.43%, Si 0.80~1.20%, Mn 0.30~
0.50%, Cr 5.10~5.60%, Mo 1.30~1.60%, V 0.80~1.20%, P≤0.020%, S≤0.003%, O≤
0.005%, N≤0.015%, remaining is Fe and inevitable impurity.
3. the heat treatment process according to claim 1 or 2 for improving H13 steel annealed structure uniformity, it is characterised in that: institute
The sectional dimension of H13 steel after stating forging is 90~170mm of φ.
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| CN113718092A (en) * | 2021-08-06 | 2021-11-30 | 山西太钢不锈钢股份有限公司 | Homogenization treatment method of bamboo leaf-shaped annealed tissue |
| CN114774762A (en) * | 2022-04-21 | 2022-07-22 | 江苏永钢集团有限公司 | Production method of H13 hot-work die steel bar with good low-power quality |
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| CN114774762A (en) * | 2022-04-21 | 2022-07-22 | 江苏永钢集团有限公司 | Production method of H13 hot-work die steel bar with good low-power quality |
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| CN110317934B (en) | 2021-08-24 |
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