CN110218949A - The method of carburizing temperature and the case-carbonizing method of mild steel are improved using microalloying - Google Patents
The method of carburizing temperature and the case-carbonizing method of mild steel are improved using microalloying Download PDFInfo
- Publication number
- CN110218949A CN110218949A CN201910630615.5A CN201910630615A CN110218949A CN 110218949 A CN110218949 A CN 110218949A CN 201910630615 A CN201910630615 A CN 201910630615A CN 110218949 A CN110218949 A CN 110218949A
- Authority
- CN
- China
- Prior art keywords
- steel
- grain size
- carburizing
- low
- mild steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Classifications
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/20—Carburising
- C23C8/22—Carburising of ferrous surfaces
Abstract
The invention belongs to mild steel or low-carbon alloy steel carburizing technical field of heat treatment, in particular to the case-carbonizing method of a kind of method and mild steel that carburizing temperature is improved using microalloying.The method is to choose mild steel of the carbon content less than 0.25% or low-carbon alloy Steel material, carry out design of alloy, the combination of Nb or Ti or Nb and V or the combination of Ti and V or the combination microalloy element of Nb and Ti and V are added in addition in smelting process in smelting process, to improve the carburizing temperature of mild steel or low-carbon alloy steel, to further increase carburizing rate, shorten the carburization process period, reduces energy consumption.
Description
Technical field
The present invention relates to mild steel or low-carbon alloy steel carburizing technical field of heat treatment, in particular to a kind of to utilize microalloy
Change the case-carbonizing method of the method and mild steel that improve carburizing temperature.
Background technique
Carburizing is the process for instigating carbon atom to penetrate into steel surface layer.And make mild steel (phosphorus content is less than 0.25%)
Workpiece has the superficial layer of high-carbon steel, using quenching and lonneal, the superficial layer of workpiece is made to have high rigidity and wearability,
And the central part of workpiece still remains the toughness and plasticity of mild steel simultaneously.
High-temperature carburizing has the characteristics that environmental protection, efficient, low cost, is one of the important directions of carburizing tech development.It improves
Carburizing temperature can significantly increase the diffusion rate of active atoms of carbon in carburizing process, reduce diffusion time, improve production effect
Rate, saves energy consumption and production cost.Studies have shown that when one timing of carburized (case) depth, the higher carburizing time of carburizing temperature
It is shorter.It is estimated that 6h is needed when 930 DEG C of gear surface carburizing reaches the carburized (case) depth of 1mm, and only in 1050 DEG C of carburizings
Need 2h.Therefore, it is needed for environmental protection, energy conservation, production efficiency etc., the future development of carburizing tech will be become using high-temperature carburizing
Direction.
But at the same time, carburizing temperature, which is increased to after a certain range, will cause austenite grain and excessively grows up, unavoidably
Ground will appear grain coarsening phenomenon.Autstenitic grain size is closely related with austenitizing temperature, and temperature is higher, and austenite grain is got over
Coarse, the martensite that carburizing terminates to obtain after quenching also can be coarse.And massive martensite tissue will lead to part and actually use
When, intensity decline, plasticity is deteriorated, is easily deformed and cracks, the fatigue behaviour of material is substantially reduced, the service life of part
It is remarkably decreased.Therefore, how to solve the problems, such as during high-temperature carburizing that AUSTENITE GRAIN COARSENING is grown up is high-temperature carburizing technology hair
The key of exhibition.
Existing patent mentions the Coarsening Temperature that austenite grain can be improved by Nb, Al microalloying (i.e. in Xiang Tongwen
Can fining austenite grains under degree), so that the carburizing temperature of low-carbon alloy steel be made to be increased to 1050 DEG C.But due in steel exist compared with
The Al of high-content2O3, every anti-fatigue performance of low-carbon alloy steel is easily reduced, while because of Al when smelting molten steel2O3Presence and band
To be poured difficult problem.
Summary of the invention
(1) technical problems to be solved
The object of the present invention is to provide a kind of methods for improving carburizing temperature using microalloying, by mild steel or low
Microalloy element is added in carbon alloy steel, to improve the carburizing temperature of mild steel or low-carbon alloy steel to improve carburizing speed,
To solve the problems such as carburizing temperature is low, process cycle is long and energy-output ratio is big in traditional carburizing heat treatment process.
(2) technical solution
On the one hand, the application provides a kind of method for improving carburizing temperature using combined microalloying, and method is:
Mild steel of the carbon content less than 0.25% or low-carbon alloy Steel material are chosen, carries out design of alloy, is smelting
The combination of Nb or Ti or Nb and V or the combination of Ti and V or the combination microalloy element of Nb and Ti and V are added in the process, with
Improve the carburizing temperature of mild steel or low-carbon alloy steel.
Preferably, in the mild steel or low-carbon alloy steel after making to add microalloy element, the content of Nb is 0.02~
0.06%.
Preferably, in the mild steel or low-carbon alloy steel after making to add microalloy element, the content of Ti is 0.01~
0.05%.
Preferably, in the mild steel or low-carbon alloy steel after making to add microalloy element, the content of V is 0.01~
0.06%.
Preferably, in the mild steel or low-carbon alloy steel after making to add microalloy element, the content of Nb is 0.02~
0.06%, the content of Ti is 0.01~0.05%, the content of V is 0.01~0.06%.
Preferably, Mo element is contained in the low-carbon alloy Steel material.
On the other hand, the application also provides a kind of case-carbonizing method of mild steel comprising:
S1: choosing mild steel of the carbon content less than 0.25% or low-carbon alloy Steel material, carries out design of alloy, in smelting
Combination, the combination of Ti and V or the combination microalloy element of Nb and Ti and V that Nb, Ti, Nb and V are added during refining, make low-carbon
Microalloying is realized inside steel；
S2: to the mild steel of microalloying, its austenite grain ruler under the conditions of different temperatures and soaking time is measured
It is very little, and grain size number is calculated, carburizing temperature upper limit value is determined under the premise of guaranteeing austenite grain size without obvious roughening；
S3: case-carbonizing is carried out within the temperature range of determining carburizing temperature upper limit value.
Preferably, in step S2, in step S2, refer to without obvious roughening according to GB/T6394-2002 " the average crystalline substance of metal
Particle size determination ", using resection calculate grain size, obtain average grain size and rank, when grain size number be 8 grades with
When upper, it was determined as austenite grain size without obvious roughening.
The principle of the present invention program are as follows:
The present invention has fully considered the thermokinetics condition of microalloy Solid Solution of Second Phase Particles and precipitation, microalloy Nb, Ti,
V is strong carbonitride-forming elements, can be formed in conjunction with C, N in steel as matrix material Nb (C, N), Ti (C, N), (Nb, Ti)
(C, N), the Carbonitride Precipitation phase of the small and disperseds such as V (C, N), these disperse educts mutually have certain high-temperature stability, need
Higher temperature and longer time ability sufficiently back dissolving are into steel as matrix material.When in material composition simultaneously containing the elements such as Mo
When, more complicated disperse educt phase can also be formed, such as (Nb, Mo) (C, N) and (Ti, Mo) (C, N) phase, had preferably thin
Brilliant effect.Nanometer microalloy carbonitride grows up to austenite grain boundary under conditions of high temperature is not dissolved completely to be made with pinning
With, can play inhibit grain coarsening effect, to guarantee to improve carburizing temperature under the premise of high temperature crystal granularity.
(3) beneficial effect
The beneficial effects of the present invention are:
The present invention is directed to the carburizing Steel material of low-carbon, using the means of microalloying, by addition microalloy element (Nb,
The combination of Ti, Nb and V, the combination of Ti and V or the combination of Nb and Ti and V) and content is controlled, utilize microalloy carbonitride
Pinning effect inhibits AUSTENITE GRAIN COARSENING to grow up during high-temperature carburizing.
The present invention can improve carburizing under the premise of guaranteeing that crystallite dimension is not roughened on the basis of conventional process conditions
10~100 DEG C of temperature, while correspondingly reducing diffusion time；Shorten carburizing heat treatment process by accelerating carbon spread rate
Energy consumption is greatly reduced in period, saves production cost, and is generally applicable to production carburizing bearing steel and carburized gears steel
Material.Experiment shows that production efficiency 5%~20% can be improved in every 10 DEG C of the raising of carburizing temperature.
The carburizing temperature of mild steel or low-carbon alloy steel not only can be improved in any combination of vanadium and vanadium and Ti or/and Nb
To increase carburizing rate, while when the alloy attribute by vanadium or Ti and Nb optimizes adjustment to steel other properties, tool
There are many combining form and wider array of flexibility in use, to meet specific steel design requirement.
In conclusion microalloying design is carried out under traditional carburizing bearing steel and the component system of carbonized Gear Steel, it can
To hinder AUSTENITE GRAIN COARSENING to grow up under the high temperature conditions, high-temperature carburizing is realized, improves production efficiency, reduce development cost,
Achieve the purpose that energy-saving and emission-reduction greenization produces.
Detailed description of the invention
Fig. 1 is the tissue topography that experiment steel keeps the temperature 4 hours under the conditions of 1050 DEG C in embodiment 1.
Fig. 2 is the tissue topography that experiment steel keeps the temperature 4 hours under the conditions of 1100 DEG C in embodiment 1.
Fig. 3 is the tissue topography that experiment steel keeps the temperature 8 hours under the conditions of 960 DEG C in embodiment 2.
Fig. 4 is the tissue topography that experiment steel keeps the temperature 8 hours under the conditions of 1050 DEG C in embodiment 2.
Fig. 5 is the tissue topography that experiment steel keeps the temperature 8 hours under the conditions of 1000 DEG C in embodiment 3.
Fig. 6 is the tissue topography that experiment steel keeps the temperature 2 hours under the conditions of 1200 DEG C in embodiment 3.
Fig. 7 is the carburizing pulsation process (correlation with carburizing temperature) using vacuum low-pressure.
Fig. 8 is the tissue topography that experiment steel keeps the temperature 4 hours under the conditions of 1050 DEG C in embodiment 4.
Fig. 9 is the tissue topography that experiment steel keeps the temperature 2 hours under the conditions of 1200 DEG C in embodiment 4.
Figure 10 is the tissue topography that the experiment steel of embodiment 5 keeps the temperature 4 hours under the conditions of 1000 DEG C.
Figure 11 is the tissue topography that the experiment steel of embodiment 5 keeps the temperature 2 hours under the conditions of 1150 DEG C.
Specific embodiment
Specific implementation case is set forth below, and the present invention will be described, and following implementation process is served only for doing into one the present invention
Step explanation, it is not intended to limit the protection scope of the present invention, the change of other some non-intrinsically safes made according to the present invention and tune
Section is still scope.
Embodiment 1
Wind-powered electricity generation, harbour retarder and express locomotive etc. are widely used in using the workpiece that 18CrNiMo7-6 carburizing steel produces
Industry.18CrNiMo7-6 tests the primary chemical of steel into 0.17%C, 0.18%Si, 0.60%Mn, 1.50%Cr, 1.48%
Ni, 0.30%Mo.The 18CrNiMo7-6 steel of this chemical component is subjected to microalloying design, Nb is added, contains Nb in alloy
Amount is 0.06%.
Grain size determination then is carried out to the 18CrNiMo7-6 steel curved beam after microalloying.Experiment steel curved beam is placed in very
In empty furnace, holding temperature is warming up to furnace, after held for some time, oil quenching of coming out of the stove.Quenched sample carries out metallographic preparation, rotten
Crystal boundary is obtained after erosion significantly to organize, and carries out grain size determination.
Experiment condition: holding temperature is respectively 900 DEG C, 950 DEG C, 1000 DEG C, 1050 DEG C, 1100 DEG C, 1150 DEG C；Heat preservation
Time is respectively 0.5h, 1h, 2h and 4h, carries out 24 experiments altogether.
Grain boundary corrosion method: saturation picric acid solution is heated to 67 DEG C, is added a small amount of hair cream, after stirring and dissolving, will polish
Sample immerses corrosion 2-3 minutes afterwards, is then rinsed with water, and observes after spray alcohol drying.
Grain size testing standard: it according to GB/T6394-2002 " metal mean grain size measuring method ", is surveyed using resection
Grain size is calculated, average grain size and rank are obtained.
Fig. 1 is the tissue topography tested steel and keep the temperature 4 hours under the conditions of 1050 DEG C, and average grain size size is 14.16 μ
M, 9 grades of grain size number.Fig. 2 is the tissue topography tested steel and keep the temperature 4 hours under the conditions of 1100 DEG C, average grain size size
It is 56.15 μm, 5 grades of grain size number, has occurred and that obvious roughening.Therefore, carburizing temperature is determined at 1050 DEG C or less.
The technique that vacuum low-pressure carburization is used to experiment steel, using multistage pulse mode carburizing, carburizing temperature is respectively 950
℃,1050℃.Under conditions of reaching identical depth of penetration and quality layer, carburizing time is 4h and 1.6h respectively.With infiltration
The raising of carbon temperature, carburizing time are obviously shortened, and carburizing time, which improves 100 DEG C, can about make production efficiency improve 60%.
Embodiment 2
20CrMn carburizing steel is widely used in high speed, high load capacity and gear shaft, gear, water without thump working under load
On the structural members such as pump rotor, clutch, small axis, mandrel and bolt.The primary chemical of steel is tested into 0.18%C, 0.20%Si,
1.05%Mn, 1.17%Cr.The 20CrMn steel of this chemical component is subjected to microalloying design, Ti is added, contains Ti in alloy
Amount is 0.06%, just obtains the highest 20CrMnTi carburizing steel of current China market occupation rate.
Grain size determination then is carried out to 20CrMnTi steel curved beam.Experiment steel curved beam is placed in vacuum drying oven, is heated up with furnace
To holding temperature, after held for some time, oil quenching of coming out of the stove.Quenched sample carries out metallographic preparation, and it is bright to obtain crystal boundary after corrosion
Aobvious tissue carries out grain size determination.
Experiment condition: holding temperature is respectively 900 DEG C, 930 DEG C, 960 DEG C, 1000 DEG C, 1050 DEG C, 1100 DEG C；When heat preservation
Between be respectively 1h, 2h, 4h and 8h, altogether carry out 24 times experiment.
Grain boundary corrosion method: saturation picric acid solution is heated to 65 DEG C, is added a small amount of hair cream, after stirring and dissolving, will polish
Sample immerses corrosion 2-3 minutes afterwards, is then rinsed with water, and observes after spray alcohol drying.
Grain size testing standard: it according to GB/T6394-2002 " metal mean grain size measuring method ", is surveyed using resection
Grain size is calculated, average grain size and rank are obtained.
Fig. 3 is the tissue topography tested steel and keep the temperature 8 hours under the conditions of 960 DEG C, and average grain size size is 19.79 μ
M, 8 grades of grain size number.Fig. 4 is the tissue topography tested steel and keep the temperature 8 hours under the conditions of 1050 DEG C, and average grain size is big
Small is 55.17 μm, 5 grades of grain size number, has occurred and that obvious roughening.Therefore, carburizing temperature determination is at 960 DEG C and following.
Embodiment 3
17Cr2Ni2Mo steel is the production domesticization trade mark of the Cr-Ni-Mo system pinion steel of ZF company exploitation, is widely used in system
Make the driving members such as gear, bevel gear, retarder part, butterfly wheel, friction member etc..The primary chemical of steel is tested into 0.18%C,
0.22%Si, 0.55%Mn, 1.65%Cr, 1.70%Ni, 0.28%Mo.The 17Cr2Ni2Mo steel of this chemical component is carried out
Microalloying design, adds the combination microalloy element of Nb and V, makes Nb content 0.06% in alloy, V content 0.10%.
Grain size determination then is carried out to the 17Cr2Ni2Mo steel curved beam after microalloying.Experiment steel curved beam is placed in vacuum
In furnace, holding temperature is warming up to furnace, after held for some time, oil quenching of coming out of the stove.Quenched sample carries out metallographic preparation, corrosion
After obtain crystal boundary and significantly organize, carry out grain size determination.
Experiment condition: holding temperature is respectively 900 DEG C, 940 DEG C, 1000 DEG C, 1100 DEG C, 1200 DEG C；Soaking time difference
For 1h, 2h, 4h and 8h, 20 experiments are carried out altogether.
Grain boundary corrosion method: saturation picric acid solution is heated to 67 DEG C, is added a small amount of hair cream, after stirring and dissolving, will polish
Sample immerses corrosion 2-3 minutes afterwards, is then rinsed with water, and observes after spray alcohol drying.
Grain size testing standard: it according to GB/T6394-2002 " metal mean grain size measuring method ", is surveyed using resection
Grain size is calculated, average grain size and rank are obtained.
Fig. 5 is the tissue topography tested steel and keep the temperature 8 hours under the conditions of 1000 DEG C, and average grain size size is 19.98 μ
M, 8 grades of grain size number.Fig. 6 is the tissue topography tested steel and keep the temperature 2 hours under the conditions of 1200 DEG C, average grain size size
It is 106.2 μm, 3.2 grades of grain size number, has occurred and that obvious roughening.Therefore, carburizing temperature is determined at 1000 DEG C or less.
The technique that vacuum low-pressure carburization is used to experiment steel, using multistage pulse mode carburizing, carburizing temperature is respectively 930
℃,950℃,980℃.Carburizing pulsation process seeps as shown in fig. 7, under conditions of reaching identical depth of penetration and quality layer
The carbon time is 6.26h, 5.15h and 3.33h respectively.With the raising of carburizing temperature, carburizing time is obviously shortened, and carburizing time is every
Improving 10 DEG C can about make production efficiency improve 14%~17%.
Embodiment 4
Bending strength with higher and wear-resisting property after 20CrMnMo steel carburizing and quenching are usually used in manufacturing high rigidity, height
The larger important carburizing part of intensity, high tenacity, such as crankshaft, camshaft, connecting rod, gear shaft, gear, pin shaft.Test the master of steel
Want chemistry at 0.23%C, 0.18%Si, 1.20%Mn, 1.35%Cr, 0.26%Mo.By the 20CrMnMo steel of this chemical component
Microalloying design is carried out, 0.06%Nb, 0.03%V and 0.015%Ti are added.
Grain size determination then is carried out to the 20CrMnMo steel curved beam after microalloying.Experiment steel curved beam is placed in vacuum drying oven
In, holding temperature is warming up to furnace, after held for some time, oil quenching of coming out of the stove.Quenched sample carries out metallographic preparation, after corrosion
It obtains crystal boundary significantly to organize, carries out grain size determination.
Experiment condition: holding temperature is respectively 950 DEG C, 1000 DEG C, 1050 DEG C, 1100 DEG C, 1200 DEG C；Soaking time difference
For 1h, 2h, 4h and 8h, 20 experiments are carried out altogether.
Grain boundary corrosion method: saturation picric acid solution is heated to 68 DEG C, is added a small amount of hair cream, after stirring and dissolving, will polish
Sample immerses corrosion 1-2 minutes afterwards, is then rinsed with water, and observes after spray alcohol drying.
Grain size testing standard: it according to GB/T6394-2002 " metal mean grain size measuring method ", is surveyed using resection
Grain size is calculated, average grain size and rank are obtained.
Fig. 8 is the tissue topography tested steel and keep the temperature 4 hours under the conditions of 1050 DEG C, and average grain size size is 13.3 μ
M, 9 grades of grain size number.Fig. 9 is the tissue topography tested steel and keep the temperature 2 hours under the conditions of 1200 DEG C, and average grain size is big
Small is 93.6 μm, 3.5 grades of grain size number, has occurred and that obvious roughening.Therefore, carburizing temperature is determined at 1050 DEG C or less.
The technique that vacuum low-pressure carburization is used to experiment steel, using multistage pulse mode carburizing, carburizing temperature is respectively
1000℃,1050℃.Under conditions of reaching identical depth of penetration and quality layer, carburizing time is 3.6h and 1.5h respectively.
With the raising of carburizing temperature, carburizing time is obviously shortened, and carburizing time, which improves 50 DEG C, can about make production efficiency improve 58.3%.
Embodiment 5
Various gears under high load capacity, alternate stress, snail are widely used in using the workpiece that 12Cr2Ni4A carburizing steel produces
The mechanical structured members such as wheel, worm screw, main shaft.12Cr2Ni4A tests the primary chemical of steel into 0.12%C, 0.25%Si, 0.4%
Mn, 1.6%Cr, 3.8%Ni.The 12Cr2Ni4A steel of this chemical component is subjected to microalloying design, Ti and V is added, makes alloy
Middle V content is 0.03% and Ti content is 0.02%.
Grain size determination then is carried out to the 12Cr2Ni4A steel curved beam after microalloying.Experiment steel curved beam is placed in vacuum
In furnace, holding temperature is warming up to furnace, after held for some time, oil quenching of coming out of the stove.Quenched sample carries out metallographic preparation, corrosion
After obtain crystal boundary and significantly organize, carry out grain size determination.
Experiment condition: holding temperature is respectively 900,930 DEG C, 950 DEG C, 1000 DEG C, 1050 DEG C, 1150 DEG C；Soaking time
Respectively 1h, 2h and 4h carry out 18 experiments altogether.
Grain boundary corrosion method: saturation picric acid solution is heated to 70 DEG C, is added a small amount of hair cream, after stirring and dissolving, will polish
Sample immerses corrosion 2-3 minutes afterwards, is then rinsed with water, and observes after spray alcohol drying.
Grain size testing standard: it according to GB/T6394-2002 " metal mean grain size measuring method ", is surveyed using resection
Grain size is calculated, average grain size and rank are obtained.
Figure 10 is the tissue topography tested steel and keep the temperature 4 hours under the conditions of 1000 DEG C, and average grain size size is 12.6 μ
M, 9.7 grades of grain size number.Figure 11 is the tissue topography tested steel and keep the temperature 2 hours under the conditions of 1150 DEG C, average grain size
Size is 86.2 μm, 4.2 grades of grain size number, has occurred and that obvious roughening.Therefore, by carburizing temperature determine 1000 DEG C with
Under.
The technique that vacuum low-pressure carburization is used to experiment steel, using multistage pulse mode carburizing, carburizing temperature is respectively 930
℃,950℃,980℃.Carburizing pulsation process seeps as shown in fig. 7, under conditions of reaching identical depth of penetration and quality layer
The carbon time is 6.26h, 5.15h and 3.33h respectively.With the raising of carburizing temperature, carburizing time is obviously shortened, and carburizing time is every
Improving 10 DEG C can about make production efficiency improve 14%~17%.
Obviously, various changes and modifications can be made to the invention without departing from essence of the invention by those skilled in the art
Mind and range.In this way, if these modifications and changes of the present invention belongs to the range of the claims in the present invention and its equivalent technologies
Within, then the present invention is also intended to include these modifications and variations.In addition, the technical characteristic in the various embodiments described above, into
Any combination under the combination of row feature and reconcilable situation, should also be included in the present invention.
Claims (8)
1. a kind of method for improving carburizing temperature using combined microalloying, which is characterized in that the method is: choosing carbon content
Mild steel or low-carbon alloy Steel material less than 0.25% carry out design of alloy, add and smelting in smelting process
The combination of Nb or Ti or Nb and V or the combination of Ti and V or the combination microalloy element of Nb and Ti and V are added in journey, to mention
The carburizing temperature of height carbon steel or low-carbon alloy steel.
2. the method according to claim 1 for improving carburizing temperature using combined microalloying, which is characterized in that make to add
In mild steel or low-carbon alloy steel after microalloy element, the content of Nb is 0.02~0.06%.
3. the method according to claim 1 for improving carburizing temperature using combined microalloying, which is characterized in that make to add
In mild steel or low-carbon alloy steel after microalloy element, the content of Ti is 0.01~0.05%.
4. the method according to claim 1 for improving carburizing temperature using combined microalloying, which is characterized in that make to add
In mild steel or low-carbon alloy steel after microalloy element, the content of V is 0.01~0.06%.
5. the method according to claim 1 for improving carburizing temperature using combined microalloying, which is characterized in that make to add
In mild steel or low-carbon alloy steel after microalloy element, the content of Nb is 0.02~0.06%, the content of Ti be 0.01~
0.05%, the content of V is 0.01~0.06%.
6. the method according to claim 1 for improving carburizing temperature using combined microalloying, which is characterized in that described low
Contain Mo element in carbon alloy steel material.
7. a kind of case-carbonizing method of mild steel characterized by comprising
S1: choosing mild steel of the carbon content less than 0.25% or low-carbon alloy Steel material, carries out design of alloy, was smelting
Combination, the combination of Ti and V or the combination microalloy element of Nb and Ti and V that Nb, Ti, Nb and V are added in journey, make in mild steel
Realize microalloying in portion；
S2: to the mild steel of microalloying, measuring its austenite grain size under the conditions of different temperatures and soaking time, and
Grain size number is calculated, determines carburizing temperature upper limit value under the premise of guaranteeing austenite grain size without obvious roughening；
S3: case-carbonizing is carried out within the temperature range of determining carburizing temperature upper limit value.
8. case-carbonizing method according to claim 7, which is characterized in that in step S2, refer to basis without obvious roughening
GB/T6394-2002 " metal mean grain size measuring method ", using resection calculate grain size, obtain average grain size and
Rank is determined as austenite grain size without obvious roughening when grain size number is 8 grades or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910630615.5A CN110218949A (en) | 2019-07-12 | 2019-07-12 | The method of carburizing temperature and the case-carbonizing method of mild steel are improved using microalloying |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910630615.5A CN110218949A (en) | 2019-07-12 | 2019-07-12 | The method of carburizing temperature and the case-carbonizing method of mild steel are improved using microalloying |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN110218949A true CN110218949A (en) | 2019-09-10 |
Family
ID=67813363
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910630615.5A Pending CN110218949A (en) | 2019-07-12 | 2019-07-12 | The method of carburizing temperature and the case-carbonizing method of mild steel are improved using microalloying |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN110218949A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113416899A (en) * | 2021-06-24 | 2021-09-21 | 马鞍山钢铁股份有限公司 | Nb and B microalloyed gear steel and preparation method, heat treatment method, carburization method and carburized gear steel thereof |
Citations (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000160288A (en) * | 1998-11-26 | 2000-06-13 | Mitsubishi Seiko Muroran Tokushuko Kk | Carburizing steel and carburized steel |
| CN100404721C (en) * | 2006-06-22 | 2008-07-23 | 钢铁研究总院 | Steel for heavy loading gear |
| CN101275204A (en) * | 2008-03-26 | 2008-10-01 | 莱芜钢铁股份有限公司 | Cr-Mn-Ti gear steel and preparation thereof |
| CN101289731A (en) * | 2008-05-09 | 2008-10-22 | 莱芜钢铁股份有限公司 | CrMnTi narrow hardenability strip pinion steels and method of manufacture |
| CN101319294A (en) * | 2008-07-22 | 2008-12-10 | 钢铁研究总院 | Steel for fine grain carburizing gear and method of manufacturing the same |
| CN102131945A (en) * | 2009-01-16 | 2011-07-20 | 新日本制铁株式会社 | Case hardening steel, carburized component, and method for producing case hardening steel |
| CN102317490A (en) * | 2009-03-30 | 2012-01-11 | 新日本制铁株式会社 | Carburized steel part |
| CN102459678A (en) * | 2009-05-27 | 2012-05-16 | 住友金属工业株式会社 | Carburized component and manufacturing method therefor |
| CN102803539A (en) * | 2010-12-08 | 2012-11-28 | 新日本制铁株式会社 | Gas-carburized steel component with excellent surface fatigue strength, gas-carburizing steel material, and process for producing gas-carburized steel component |
| CN102978562A (en) * | 2012-11-02 | 2013-03-20 | 浙江吉利汽车研究院有限公司杭州分公司 | Low-carbon alloy steel carburizing technology |
| CN103361559A (en) * | 2013-07-18 | 2013-10-23 | 首钢总公司 | Nb and Ti composite micro-alloyed high-temperature carburized gear steel |
| CN104884660A (en) * | 2012-12-28 | 2015-09-02 | 新日铁住金株式会社 | Steel for carburizing |
| CN104894353A (en) * | 2015-04-29 | 2015-09-09 | 首钢总公司 | Nb-containing high-temperature carburized gear steel rolling method |
| CN105121687A (en) * | 2013-04-18 | 2015-12-02 | 新日铁住金株式会社 | Case-hardening steel material and case-hardening steel member |
| CN108866439A (en) * | 2018-07-16 | 2018-11-23 | 东北大学 | A kind of Nb, Ti combined microalloying high-temperature vacuum carburizing heavy-duty gear steel |
| CN109763078A (en) * | 2018-05-28 | 2019-05-17 | 宝钢特钢长材有限公司 | A kind of heat-resisting alloy carburizing steel and preparation method thereof |
-
2019
- 2019-07-12 CN CN201910630615.5A patent/CN110218949A/en active Pending
Patent Citations (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000160288A (en) * | 1998-11-26 | 2000-06-13 | Mitsubishi Seiko Muroran Tokushuko Kk | Carburizing steel and carburized steel |
| CN100404721C (en) * | 2006-06-22 | 2008-07-23 | 钢铁研究总院 | Steel for heavy loading gear |
| CN101275204A (en) * | 2008-03-26 | 2008-10-01 | 莱芜钢铁股份有限公司 | Cr-Mn-Ti gear steel and preparation thereof |
| CN101289731A (en) * | 2008-05-09 | 2008-10-22 | 莱芜钢铁股份有限公司 | CrMnTi narrow hardenability strip pinion steels and method of manufacture |
| CN101319294A (en) * | 2008-07-22 | 2008-12-10 | 钢铁研究总院 | Steel for fine grain carburizing gear and method of manufacturing the same |
| CN102131945A (en) * | 2009-01-16 | 2011-07-20 | 新日本制铁株式会社 | Case hardening steel, carburized component, and method for producing case hardening steel |
| CN102317490A (en) * | 2009-03-30 | 2012-01-11 | 新日本制铁株式会社 | Carburized steel part |
| CN102459678A (en) * | 2009-05-27 | 2012-05-16 | 住友金属工业株式会社 | Carburized component and manufacturing method therefor |
| CN102803539A (en) * | 2010-12-08 | 2012-11-28 | 新日本制铁株式会社 | Gas-carburized steel component with excellent surface fatigue strength, gas-carburizing steel material, and process for producing gas-carburized steel component |
| CN102978562A (en) * | 2012-11-02 | 2013-03-20 | 浙江吉利汽车研究院有限公司杭州分公司 | Low-carbon alloy steel carburizing technology |
| CN104884660A (en) * | 2012-12-28 | 2015-09-02 | 新日铁住金株式会社 | Steel for carburizing |
| CN105121687A (en) * | 2013-04-18 | 2015-12-02 | 新日铁住金株式会社 | Case-hardening steel material and case-hardening steel member |
| CN103361559A (en) * | 2013-07-18 | 2013-10-23 | 首钢总公司 | Nb and Ti composite micro-alloyed high-temperature carburized gear steel |
| CN104894353A (en) * | 2015-04-29 | 2015-09-09 | 首钢总公司 | Nb-containing high-temperature carburized gear steel rolling method |
| CN109763078A (en) * | 2018-05-28 | 2019-05-17 | 宝钢特钢长材有限公司 | A kind of heat-resisting alloy carburizing steel and preparation method thereof |
| CN108866439A (en) * | 2018-07-16 | 2018-11-23 | 东北大学 | A kind of Nb, Ti combined microalloying high-temperature vacuum carburizing heavy-duty gear steel |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113416899A (en) * | 2021-06-24 | 2021-09-21 | 马鞍山钢铁股份有限公司 | Nb and B microalloyed gear steel and preparation method, heat treatment method, carburization method and carburized gear steel thereof |
| CN113416899B (en) * | 2021-06-24 | 2022-04-19 | 马鞍山钢铁股份有限公司 | Nb and B microalloyed gear steel and preparation method, heat treatment method, carburization method and carburized gear steel thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN104630634B (en) | The excellent carburizing steel of forging and its manufacture method | |
| CN105899697B (en) | The manufacture method and carburizing steel part of carburizing steel part | |
| CN102226252B (en) | High-toughness carburized bearing steel with ultra-long contact fatigue life and preparation method thereof | |
| CN100510146C (en) | Spring steel with excellent resistance to hydrogen embrittlement and steel wire and spring obtained from the steel | |
| RU2425171C2 (en) | Forging steel | |
| CN102066586B (en) | Process for production of carburized part and steel part | |
| JPH0426752A (en) | Rolling bearing | |
| CN100389229C (en) | Boron-Chromium-rare earth co-infiltration process combined with pre-infiltration cold deformation for workpiece | |
| CN108559922B (en) | A kind of rock tunnel(ling) machine hobboing cutter cutter ring alloy material and preparation method thereof | |
| CN100455698C (en) | Surface-carbonitrided stainless steel parts excellent in wear resistance and method for their manufacture | |
| CN101970704A (en) | Rolling component and manufacturing method thereof | |
| CN108866439A (en) | A kind of Nb, Ti combined microalloying high-temperature vacuum carburizing heavy-duty gear steel | |
| CN101880833A (en) | Stainless bearing steel adopting microalloying of rare earth and applicable to manufacturing miniature and small-size bearings and manufacturing method thereof | |
| Wang et al. | Effects of boronizing treatment on corrosion resistance of 65Mn steel in two acid mediums | |
| JP2009127095A (en) | Case-hardening steel for power transmission component | |
| CN110218949A (en) | The method of carburizing temperature and the case-carbonizing method of mild steel are improved using microalloying | |
| CN101880851B (en) | Novel method for carrying out low-temperature surface catalysis and nitriding on alloy cast iron | |
| CN107761048A (en) | The method that N C V Mo RE multicomponent thermochemical treatments strengthen steel material surface | |
| CN109881122A (en) | Big tilling depth rotary blade material of abrasion resistant and corrosion resistant and preparation method thereof | |
| CN107299294A (en) | High-strength spring steel with excellent corrosion resistance | |
| US20090035602A1 (en) | High-strength steel with excellent unsusceptibility to hydrogen embrittlement | |
| US11952668B2 (en) | Carburized part and method for manufacturing same | |
| CN114959553A (en) | Heat treatment method for improving metal surface carbonization performance | |
| KR20150074645A (en) | Material for high carburizing steel and method for producing gear using the same | |
| CN108220805A (en) | The excellent steel wire for high strength spring of anticorrosion stress-resistant and its manufacturing method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20190910 |
|
| RJ01 | Rejection of invention patent application after publication |