CN103333997A - Annealing heat treatment method of H13 die steel - Google Patents
Annealing heat treatment method of H13 die steel Download PDFInfo
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- CN103333997A CN103333997A CN2013102731933A CN201310273193A CN103333997A CN 103333997 A CN103333997 A CN 103333997A CN 2013102731933 A CN2013102731933 A CN 2013102731933A CN 201310273193 A CN201310273193 A CN 201310273193A CN 103333997 A CN103333997 A CN 103333997A
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Abstract
The invention discloses an annealing heat treatment method of H13 die steel. The method comprises the following steps of: cooling a forged H13 die to 480-520 DEG C by using air; heating the H13 die in a heat treatment furnace to 530-570 DEG C along with the furnace; preserving heat for 3-5 hours so that the die temperature is uniform; after the first-stage heat treatment and the second-stage heat treatment, cooling to 350-400 DEG C along with the furnace; and discharging and performing air cooling to finish the heat treatment. The method disclosed by the invention improves the carbide spheroidization rate which can exceed 95%; and moreover, the carbide distribution is uniform and fine, and the segregation of alloy elements is improved so that the die hardness of the die is more uniform.
Description
Technical field
The invention belongs to heat treating method, specifically refer to a kind of annealing heat treating method of H13 die steel.
Technical background
Alloying element content in the H13 die steel reaches about 8%, the interpolation of a large amount of alloying elements moves to left eutectoid point, H13 die steel belongs to hypereutectoid steel, the macrosegregation of carbon and alloying element, the particularly effect of chromium, v element makes this steel unbalanced meta eutectic carbides occur in process of setting.The H13 die steel annealed state core structure of at present a lot of domestic productions exists thick eutectic carbides and component segregation, proeutectoid carbide accumulates in the crystal boundary place, and be linked to be chain-like carbide in the local area, and eutectic carbides and proeutectoid carbide are assembled to the impact toughness influence of module at crystal boundary very big.
Because conventional carbide annealing process because of Heating temperature lower (about 860 ℃), is difficult to improve form, distribution and the inhomogeneity of structure of carbide, especially large-sized module.Increase a normalizing treatment before the thermal treatment of routine, can reduce undissolved carbide quantity in the steel, refine austenite crystal grain alleviates the ununiformity of distribution of carbides, improves intensity and toughness.But in the thermal treatment process of present this normalizing+Spheroidizing Annealing, temperature relatively low (960 ~ 980 ℃), the soaking time of normalizing heating are relatively lacked (2h), the segregation of alloying element can not fully improve, carbide can not be dissolved in the austenite fully, therefore carbide nodularization fully when causing spheroidizing exists problems such as segregation and nodularization rate are low in the tissue.
Summary of the invention
The annealing heat treating method that the purpose of this invention is to provide a kind of H13 die steel, this method have improved the nodularization rate of carbide, have reduced the segregation of alloying element in tissue.
For achieving the above object, the annealing heat treating method of the H13 die steel that the present invention is designed may further comprise the steps:
1) the H13 module air cooling to 480 after will forging ~ 520 ℃, this temperature in case produce martensitic transformation, is put into heat treatment furnace then more than martensite point, be warming up to 530 ~ 570 ℃ with stove, and insulation 3 ~ 5h makes the module temperature even;
2) thermal treatment of fs: furnace temperature is risen to 1000 ~ 1040 ℃, insulation 8 ~ 10h, be incubated for a long time at high temperature and can be conducive to carbide and fuse in the austenite, be conducive to the diffusion of alloying element, reach the effect that improves segregation, module is taken out in stove, cold by abrupt wind speed, make the module temperature be cooled to 350 ~ 450 ℃, this temperature is more than martensite point, alloying element is evenly distributed on the matrix, and air-cooled being conducive to forms tiny carbide particle and matrix rapidly, breaks carbide network;
3) again with step 2) in the cooling the H13 module put in the heat treatment furnace, the control rate of heating makes the H13 module be heated to 630 ~ 680 ℃, insulation 3 ~ 5h avoids in follow-up heat-processed because the excessive temperature differentials on heart portion and surface causes thermal stresses and structural stress;
4) thermal treatment of subordinate phase: step 3) H13 module is heated to 810 ~ 830 ℃ with heat treatment furnace, insulation 10 ~ 15h, make the further nodularization of carbide complete, the cooling of control heat treatment furnace also makes the H13 module be cooled to 630 ~ 670 ℃, insulation 3 ~ 5h makes heart portion and surperficial temperature uniformity, cools to 350 ~ 400 ℃ with the furnace, the air cooling of coming out of the stove is finished thermal treatment.
Further, in the described step 1), the furnace temperature of heat treatment furnace≤300 ℃.
Again further, in the described step 4), the heat treatment furnace speed of cooling is 5 ~ 30 ℃/h.
Advantage of the present invention is as follows:
H13 module air cooling to 480 after the present invention will forge ~ 520 ℃, this temperature are more than martensite point, in case produce martensitic transformation; Normalizing temperature is brought up to 1000 ~ 1040 ℃, and this is conducive to, and carbide fuses in the austenite, the diffusion of alloying element, has improved the segregation of alloying element, and the liquation carbide is fused fully.The type of cooling that normalizing is adopted is for air-cooled rapidly, can make the carbide of fusion separate out fast and do not grow up, and is evenly distributed on the matrix, the carbide of separating out is tiny, breaks netted and carbide chain, and alloying element has little time diffusion, segregation is significantly improved, and organizes also to have obtained refinement.In Spheroidizing Annealing process subsequently, carbide nodularization on the tiny and uniform carbide after the normalizing, because the carbide after the normalizing is tiny, even, the efficient of Spheroidizing Annealing and nodularization rate height, the nodularization rate can reach more than 95%, and tissue is what the tissue in normalizing changed, and the tissue after the annealing will be more tiny.
Description of drawings
Fig. 1 is thermal treatment process figure of the present invention;
The high power metallographic structure figure that Fig. 2 obtains for thermal treatment process of the present invention, its tissue can reach the above rank of AS3 of North America transfer mold metallographic standard.
Among the figure, air cooling to 480 after 1. forging ~ 520 ℃; 2. stove is interior 530 ~ 570 ℃, samming 3 ~ 5h; 3. heat-up rate in the stove≤100 ℃/h; 4. stove is interior 1000 ~ 1040 ℃, insulation 8 ~ 10h; 5. taking-up module, the cold or spray cooling of strong wind speed makes module be cooled to 350 ~ 450 ℃ of the above temperature of martensite point; 6. module is put into and risen to 400 ℃ heat treatment furnace in advance;
7. heat-up rate in the control stove≤100 ℃/h; 8. stove is interior 630 ~ 680 ℃, insulation 3 ~ 5h; 9. heat-up rate in the control stove≤100 ℃/h; 10. stove is interior 810 ~ 830 ℃, insulation 10 ~ 15h;
11. control stove internal cooling speed≤30 ℃/h; 12. interior 630 ~ 670 ℃ of stove, insulation 3 ~ 5h; 13. cool to 350 ~ 400 ℃ with the furnace, the air cooling of coming out of the stove.
Embodiment
Be described in further detail below in conjunction with the annealing heat treating method of specific embodiment to H13 die steel of the present invention.
Embodiment 1
Select the H13 module of the φ 500 * 2500mm after the forging for use, concrete thermal treatment process is as follows:
1) the H13 module air cooling to 500 after will forging ℃ is put into furnace temperature and is 270 ℃ heat treatment furnace then, is warming up to 550 ℃ with stove, and insulation 3h makes the module temperature even;
2) thermal treatment of fs: furnace temperature is risen to 1020 ℃, and insulation 9h carries out module is taken out in stove, and is cold by abrupt wind speed, makes module be cooled to 400 ℃ of the temperature of martensite point;
3) again with step 2) in the cooling the H13 module put in the heat treatment furnace, control rate of heating make the H13 module be heated to 650 ℃, the insulation 4h;
4) thermal treatment of subordinate phase: step 3) H13 module is heated to 820 ℃ with heat treatment furnace, insulation 10h, and control heat treatment furnace speed of cooling is 30 ℃/h, make the H13 module be cooled to 650 ℃, insulation 4h cools to 350 ℃ with the furnace, the air cooling of coming out of the stove is finished thermal treatment.
To the metallographic structure of the H13 module after the thermal treatment as shown in Figure 2, be organized as equally distributed globular carbide on the ferrite among the figure.
Embodiment 2
Select the H13 module of the φ 500 * 2500mm after the forging for use, concrete thermal treatment process is as follows:
1) the H13 module air cooling to 520 after will forging ℃ is put into furnace temperature and is 300 ℃ heat treatment furnace then, is warming up to 570 ℃ with stove, and insulation 5h makes the module temperature even;
2) thermal treatment of fs: furnace temperature is risen to 1040 ℃, and insulation 8h carries out module is taken out in stove, and is cold by abrupt wind speed, makes module be cooled to 450 ℃ of the temperature of martensite point;
3) again with step 2) in the cooling the H13 module put in the heat treatment furnace, control rate of heating make the H13 module be heated to 630 ℃, the insulation 5h;
4) thermal treatment of subordinate phase: step 3) H13 module is heated to 830 ℃ with heat treatment furnace, insulation 12h, and control heat treatment furnace speed of cooling is 5 ℃/h, makes the H13 module be cooled to 630 ℃, and insulation 5h cools to 380 ℃ with the furnace, and the air cooling of coming out of the stove is finished thermal treatment.
Embodiment 3
Select the H13 module of the φ 500 * 2500mm after the forging for use, concrete thermal treatment process is as follows:
1) the H13 module air cooling to 480 after will forging ℃ is put into furnace temperature and is 100 ℃ heat treatment furnace then, is warming up to 530 ℃ with stove, and insulation 4h makes the module temperature even;
2) thermal treatment of fs: furnace temperature is risen to 1000 ℃, and insulation 10h carries out module is taken out in stove, and is cold by abrupt wind speed, makes module be cooled to 350 ℃ of the temperature of martensite point;
3) again with step 2) in the cooling the H13 module put in the heat treatment furnace, control rate of heating make the H13 module be heated to 680 ℃, the insulation 3h;
4) thermal treatment of subordinate phase: step 3) H13 module is heated to 810 ℃ with heat treatment furnace, insulation 15h, and control heat treatment furnace speed of cooling is 10 ℃/h, make the H13 module be cooled to 670 ℃, insulation 3h cools to 400 ℃ with the furnace, the air cooling of coming out of the stove is finished thermal treatment.
Claims (3)
1. the annealing heat treating method of a H13 die steel is characterized in that: may further comprise the steps:
1) the H13 module air cooling to 480 after will forging ~ 520 ℃ is put into heat treatment furnace then, is warming up to 530 ~ 570 ℃ with stove, and insulation 3 ~ 5h makes the module temperature even;
2) thermal treatment of fs: furnace temperature is risen to 1000 ~ 1040 ℃, and insulation 8 ~ 10h carries out module is taken out in stove, and is cold by abrupt wind speed, makes the module temperature be cooled to 350 ~ 450 ℃;
3) again with step 2) in the cooling the H13 module put in the heat treatment furnace, control rate of heating make the H13 module be heated to 630 ~ 680 ℃, the insulation 3 ~ 5h;
4) thermal treatment of subordinate phase: the H13 module is heated to 810 ~ 830 ℃ with heat treatment furnace in the step 3), insulation 10 ~ 15h, and the cooling of control heat treatment furnace also makes the H13 module be cooled to 630 ~ 670 ℃, insulation 3 ~ 5h, cool to 350 ~ 400 ℃ with the furnace, the air cooling of coming out of the stove is finished thermal treatment.
2. according to the annealing heat treating method of the described H13 die steel of claim 1, it is characterized in that: in the described step 1), the furnace temperature of heat treatment furnace≤300 ℃.
3. according to the annealing heat treating method of claim 1 or 2 described H13 die steel, it is characterized in that: in the described step 4), the heat treatment furnace speed of cooling is 5 ~ 30 ℃/h.
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103572022A (en) * | 2013-11-07 | 2014-02-12 | 大冶特殊钢股份有限公司 | Heat-treatment method for H13 section steel |
| CN104726659A (en) * | 2015-02-10 | 2015-06-24 | 中原特钢股份有限公司 | Thermal treatment process for improving microscopic coarse grains and microstructures of H13 forged piece |
| CN105414425A (en) * | 2015-11-04 | 2016-03-23 | 武汉重工铸锻有限责任公司 | Forging method capable of eliminating coarse grains in forge piece and obtaining uniform and fine grain structure |
| CN106811580A (en) * | 2017-02-13 | 2017-06-09 | 钢铁研究总院 | A kind of annealing process of H13 hot die steels |
| CN108193023A (en) * | 2017-12-01 | 2018-06-22 | 内蒙古北方重工业集团有限公司 | The method for eliminating net carbide in H13 mould steel annealing microscopic structure |
| CN108823381A (en) * | 2018-07-12 | 2018-11-16 | 河钢股份有限公司 | A kind of heat treatment process improving H13 hot-work die steel forging material structural homogenity |
| CN109161668A (en) * | 2018-09-11 | 2019-01-08 | 武钢集团襄阳重型装备材料有限公司 | A kind of H13 steel double-fined treatment technique |
| CN109852777A (en) * | 2019-01-18 | 2019-06-07 | 西华大学 | A kind of H13 mould steel and its heat treatment process |
| 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 |
| WO2020177325A1 (en) | 2019-03-01 | 2020-09-10 | 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 |
| 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 |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1540001A (en) * | 2003-11-01 | 2004-10-27 | 湖南科技大学 | Isothermal spheroidizing technique for H13 steel |
| JP2008202078A (en) * | 2007-02-19 | 2008-09-04 | Daido Steel Co Ltd | Hot-working die steel |
| CN102206739A (en) * | 2011-05-04 | 2011-10-05 | 上海大学 | Dual-refinement treatment process of hot mould steel structure |
| CN102650020A (en) * | 2012-05-14 | 2012-08-29 | 上海大学 | High-silicon high-manganese type high-thermal stability hot work die steel and thermal treatment process thereof |
| CN103173597A (en) * | 2013-02-28 | 2013-06-26 | 辽宁金钢重型锻造有限公司 | Method for improving optional performances of large H13 steel hot-extrusion mould |
-
2013
- 2013-07-02 CN CN201310273193.3A patent/CN103333997B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1540001A (en) * | 2003-11-01 | 2004-10-27 | 湖南科技大学 | Isothermal spheroidizing technique for H13 steel |
| JP2008202078A (en) * | 2007-02-19 | 2008-09-04 | Daido Steel Co Ltd | Hot-working die steel |
| CN102206739A (en) * | 2011-05-04 | 2011-10-05 | 上海大学 | Dual-refinement treatment process of hot mould steel structure |
| CN102650020A (en) * | 2012-05-14 | 2012-08-29 | 上海大学 | High-silicon high-manganese type high-thermal stability hot work die steel and thermal treatment process thereof |
| CN103173597A (en) * | 2013-02-28 | 2013-06-26 | 辽宁金钢重型锻造有限公司 | Method for improving optional performances of large H13 steel hot-extrusion mould |
Non-Patent Citations (2)
| Title |
|---|
| 杜广超: "H13钢锻后热处理工艺", 《金属热处理》 * |
| 顾佳羽等: "高温正火对H13钢锻后组织的影响", 《金属热处理》 * |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103572022A (en) * | 2013-11-07 | 2014-02-12 | 大冶特殊钢股份有限公司 | Heat-treatment method for H13 section steel |
| CN103572022B (en) * | 2013-11-07 | 2015-05-13 | 大冶特殊钢股份有限公司 | Heat-treatment method for H13 section steel |
| CN104726659A (en) * | 2015-02-10 | 2015-06-24 | 中原特钢股份有限公司 | Thermal treatment process for improving microscopic coarse grains and microstructures of H13 forged piece |
| CN105414425A (en) * | 2015-11-04 | 2016-03-23 | 武汉重工铸锻有限责任公司 | Forging method capable of eliminating coarse grains in forge piece and obtaining uniform and fine grain structure |
| CN106811580A (en) * | 2017-02-13 | 2017-06-09 | 钢铁研究总院 | A kind of annealing process of H13 hot die steels |
| CN108193023A (en) * | 2017-12-01 | 2018-06-22 | 内蒙古北方重工业集团有限公司 | The method for eliminating net carbide in H13 mould steel annealing microscopic structure |
| CN108823381A (en) * | 2018-07-12 | 2018-11-16 | 河钢股份有限公司 | A kind of heat treatment process improving H13 hot-work die steel forging material structural homogenity |
| CN109161668A (en) * | 2018-09-11 | 2019-01-08 | 武钢集团襄阳重型装备材料有限公司 | A kind of H13 steel double-fined treatment technique |
| CN109852777A (en) * | 2019-01-18 | 2019-06-07 | 西华大学 | A kind of H13 mould steel and its heat treatment process |
| CN109852777B (en) * | 2019-01-18 | 2021-09-28 | 西华大学 | H13 die steel and heat treatment process thereof |
| WO2020177325A1 (en) | 2019-03-01 | 2020-09-10 | 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 |
| 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 |
| 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 |
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Effective date of registration: 20170308 Address after: 430415 Binjiang Road, Yangluo Development Zone, Hubei, China, No. 1, No. Patentee after: Xiangyang heavy equipment Material Co Ltd Address before: 430080 Wuchang, Hubei Friendship Road, No. A, block, floor 999, 15 Patentee before: Wuhan Iron & Steel (Group) Corp. |
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