CN106086704B - A kind of hot rolled steel plate and its preparation method and application - Google Patents
A kind of hot rolled steel plate and its preparation method and application Download PDFInfo
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- CN106086704B CN106086704B CN201610688551.0A CN201610688551A CN106086704B CN 106086704 B CN106086704 B CN 106086704B CN 201610688551 A CN201610688551 A CN 201610688551A CN 106086704 B CN106086704 B CN 106086704B
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The present invention relates to hot rolled steel plate production field, specifically disclose a kind of hot rolled steel plate and its preparation method and application, the microscopic structure of the hot rolled steel plate be austenite structure and martensitic structure, wherein, in elongate crystalline form state austenite structure content account for more than the 20% of total austenite structure content.The preparation method for the hot rolled steel plate that the present invention is provided includes：To forge the slab that is formed heated successively, roughing, finish rolling and solid solution, counted using the total deformation rate of roughing and finish rolling as 100%, the deformation rate of the roughing is 60 70%, the deformation rate of the extreme trace time deformation of the finish rolling is 8 12%.The present invention causes hot rolled steel plate to have high intensity, high-ductility at normal temperatures and while high tenacity with good low temperature and ultralow temperature performance using new controlled rolling process, is particularly suitable for applying in rocket engine.
Description
Technical field
The present invention relates to hot rolled steel plate production field, in particular it relates to a kind of hot rolled steel plate, a kind of preparation of hot rolled steel plate
Method, a kind of application of hot rolled steel plate.
Background technology
Space flight hot rolled steel plate, because its application environment influences larger to material ages, existing hot rolled steel plate can not
Meet technical requirements.Technically require the yield strength ratio of space flight hot rolled steel plate, particularly rocket engine hot rolled steel plate
Bar requires high more than 50MPa, and has while requiring hot rolled steel plate at normal temperatures with high intensity, high-ductility and high tenacity
There are good low temperature and ultralow temperature performance, to ensure high thrust and long-range carrying capacity that rocket is remarkable.What existing process was developed
Hot rolled steel plate performance indications are unstable, and yield strength qualification rate is relatively low, and only 60% or so.
Therefore, it is badly in need of providing a kind of production technology of new hot rolled steel plate, develops under yield strength qualification rate height, normal temperature
Hot rolled steel plate with good low temperature and ultralow temperature performance while with high intensity, high-ductility and high tenacity.
The content of the invention
The purpose of the present invention is to be that the hot rolled steel plate yield strength qualification rate for overcoming prior art to produce is low, hot under normal temperature
Rolled steel plate yield strength, plasticity and toughness are relatively low, and there is provided have height under a kind of normal temperature for the defect of low temperature and ultralow temperature poor-performing
Hot rolled steel plate with good low temperature and ultralow temperature performance while intensity, high-ductility and high tenacity, it is a kind of simple to operate and
The preparation method of the high hot rolled steel plate of yield strength qualification rate and the application of hot rolled steel plate.
The present inventor had found by in-depth study, to containing Fe, be not more than 0.03 weight % C, be not more than
0.15 weight % Mn, no more than 0.15 weight % Si, 9-10.3 weight % Ni, 11.5-12.5 weight % Cr, 0.5-
0.8 weight % Mo, 0.15-0.25 weight % Ti, no more than 0.2 weight % Al, no more than 0.2 weight % W, less
In 0.15 weight % V, when no more than 0.15 weight % Nb and no more than 0.2 weight % Cu slab are rolled, lead to
Cross control roughing and finish-rolling process during each stage steel plate deformation rate, preferably further control deformation temperature, can change
The crystalline phase of austenite so that account for more than the 20% of total austenite structure content in the austenite structure content for elongating crystalline form state, on
State technique increase plate hot rolling near surface and deform remained austenite content, particularly austenite content in 5-7 volume %, preferably 93-
There is high intensity, high-ductility and while high tenacity with good low temperature and ultralow during 95 volume %, under hot rolled steel plate normal temperature
Warm nature energy.The present inventor further study show that, solutionizing step produces considerable influence, control to the performance of hot rolled steel plate
Solid solubility temperature is 840-860 DEG C, and the time is that 0.5-1.5h can further improve hot rolled steel plate normal temperature, low temperature and ultralow warm nature
Energy.
Based on this, the invention provides a kind of hot rolled steel plate, on the basis of the gross weight of the hot rolled steel plate, the hot rolling
Steel plate contains：Fe, the C for being not more than 0.03 weight %, the Mn for being not more than 0.15 weight %, Si, the 9- for being not more than 0.15 weight %
10.3 weight % Ni, 11.5-12.5 weight % Cr, 0.5-0.8 weight % Mo, 0.15-0.25 weight % Ti, less
In 0.2 weight % Al, no more than 0.2 weight % W, no more than 0.15 weight % V, no more than 0.15 weight % Nb and
No more than 0.2 weight % Cu；The microscopic structure of the hot rolled steel plate be austenite structure and martensitic structure, wherein, in drawing
The austenite structure content of long crystalline form state accounts for more than the 20% of total austenite structure content.
The invention provides a kind of preparation method of hot rolled steel plate, this method includes：Slab is heated successively, slightly
Roll, finish rolling and solid solution, on the basis of the gross weight of the slab, the slab contains：Fe, the C, no for being not more than 0.03 weight %
Ni, the 11.5-12.5 weight % Cr of Mn, no more than 0.15 weight % Si, 9-10.3 weight % more than 0.15 weight %,
0.5-0.8 weight % Mo, 0.15-0.25 weight % Ti, no more than 0.2 weight % Al, no more than 0.2 weight % W,
No more than 0.15 weight % V, no more than no more than 0.15 weight % Nb and 0.2 weight % Cu, with roughing and finish rolling
Total deformation rate is 100% meter, and the deformation rate of the roughing is 60-70%, and the deformation rate of the extreme trace time deformation of the finish rolling is 8-
12%.
Present invention also offers the hot rolled steel plate produced by above-mentioned preparation method.
Present invention also offers application of the above-mentioned hot rolled steel plate in rocket engine.
The hot rolled steel plate microscopic structure that the present invention is provided is austenite structure and martensitic structure, with austenite structure content
For 100% meter, in the case where multiplication factor is 100 times of metallographic microscope, it is not less than in the austenite structure content for elongating crystalline form state
20%, and yield strength R0.2It is 790-825MPa under more than 785MPa, preferable case, impact flexibility work(is excellent in more than 78J
It is 100-130J in the case of choosing, grain size is 5-8 grades under preferable case, tensile strength is 930-1000MPa, excellent more than 4 grades
It is 940-990MPa in the case of choosing, it is 12-15.5% that elongation percentage, which is not less than under 12%, preferable case,.Therefore, the present invention is provided
Hot rolled steel plate with good low temperature and ultralow temperature performance, is highly suitable for while have high intensity, high-ductility and a high tenacity
Applied in rocket engine.
Brief description of the drawings
Accompanying drawing is, for providing a further understanding of the present invention, and to constitute a part for specification, with following tool
Body embodiment is used to explain the present invention together, but is not construed as limiting the invention.In the accompanying drawings：
Fig. 1 is that hot rolled steel plate made from the embodiment of the present invention 1 is the Ovshinsky under 100 times of metallographic microscope in multiplication factor
Body metallographic structure figure；
Fig. 2 is that hot rolled steel plate made from comparative example 1 of the present invention is the Ovshinsky under 100 times of metallographic microscope in multiplication factor
Body metallographic structure figure.
Embodiment
The embodiment to the present invention is described in detail below.It should be appreciated that described herein specific
Embodiment is merely to illustrate and explain the present invention, and is not intended to limit the invention.
The end points and any value of disclosed scope are not limited to the accurate scope or value herein, these scopes or
Value should be understood to comprising the value close to these scopes or value.For number range, between the endpoint value of each scope, respectively
It can be combined with each other between the endpoint value of individual scope and single point value, and individually between point value and obtain one or more
New number range, these number ranges should be considered as specific open herein.
According to the first aspect of the invention, the invention provides a kind of hot rolled steel plate, with the gross weight of the hot rolled steel plate
On the basis of amount, the hot rolled steel plate contains：Fe, be not more than 0.03 weight % C, be not more than 0.15 weight % Mn, be not more than
0.15 weight % Si, 9-10.3 weight % Ni, 11.5-12.5 weight % Cr, 0.5-0.8 weight % Mo, 0.15-
0.25 weight % Ti, no more than 0.2 weight % Al, no more than 0.2 weight % W, no more than 0.15 weight % V, no
Nb and no more than 0.2 weight % Cu more than 0.15 weight %；The microscopic structure of the hot rolled steel plate be austenite structure and
Martensitic structure, wherein, account for more than the 20% of total austenite structure content in the austenite structure content for elongating crystalline form state.
The elongation crystalline form state refers to the form that austenite structure is elongated by equi-axed crystal along deformation direction, i.e.,：Setting
Straight line where longest distance in irregular elongated structure is Y-axis, and the straight line vertical with straight line where longest distance is X-axis,
Length of the irregular elongated structure in Y-axis is not less than 1.1 with the length ratio in X-axis.
As depicted in figs. 1 and 2, the austenite structure structure for the hot rolled steel plate that the present invention is provided is deformed, and longitudinal direction is drawn
It is long, and the austenite structure structure for the hot rolled steel plate that prior art is provided is in the axle construction such as irregular substantially.What the present invention was provided
Hot rolled steel plate has more preferable mechanical property.
In the present invention, either in the molten steel of above-mentioned hot rolled steel plate still for preparing the steel plate, except above-mentioned element
Outside, in addition to the inevitable impurity in addition to silicon.And Fe content is usually 75-78 weight %.
A preferred embodiment of the invention, total austenite group is accounted in the austenite structure content for elongating crystalline form state
Knit the 30-40% of content.
In the austenite structure content of elongation crystalline form state by under 100 times of metallographic microscope, being calculated in multiplication factor
The length in Y-axis being observed that in statistical regions is not less than 1.1 irregular elongation with the length ratio in X-axis
Area ratio shared by grainiess is obtained.
A preferred embodiment of the invention, the content of the austenite structure is 5-7 volume %, martensite group
The content knitted is 93-95 volumes %.
In the present invention, the content of austenite structure and martensitic structure is spread out by X, pert Pro in the hot rolled steel plate
Instrument is penetrated to determine.
The thickness of the hot rolled steel plate of the present invention can be selected according to the application conditions of hot rolled steel plate.Easily controlled from plate shape
The demand angle of system and rocket engine materials sets out, and the thickness of the hot rolled steel plate is preferably 5-30mm, more preferably 5-
20mm。
A preferred embodiment of the invention, the yield strength R of the hot rolled steel plate0.2It is excellent in more than 785MPa
Elect 790-825MPa as.The yield strength R of the hot rolled steel plate0.2Detected according to method as defined in GB/T228.1-2010.
A preferred embodiment of the invention, subzero 192 DEG C of impact flexibility work(of the hot rolled steel plate 78J with
On, preferably 100-130J illustrates that the hot rolled steel plate that the present invention is provided has preferable cryogenic property.
In the present invention, subzero 192 DEG C of impact flexibility work(of the hot rolled steel plate is according to side as defined in GB/T229-2007
Method is detected.
A preferred embodiment of the invention, the grain size of the hot rolled steel plate is more than 4 grades, preferably 5-8
Level.The grain size is determined by the comparison method in GB/T 6394-2002.
A preferred embodiment of the invention, the tensile strength R of the hot rolled steel platemIt is excellent for 930-1000MPa
Elect 940-990MPa as.The tensile strength RmDetermined by GB/T228.1-2010 metal materials tensile testing at ambient temperature.
A preferred embodiment of the invention, the elongation percentage A of the hot rolled steel plate is not less than 12%, is preferably
12-15.5%.The elongation percentage A is determined by GB/T228.1-2010 metal materials tensile testing at ambient temperature.
The microscopic structure of the hot rolled steel plate of the present invention is austenite structure and martensitic structure, and by that will be in draw
The austenite structure content of long crystalline form state accounts for total austenite structure content control more than 20%, realizes the performance of hot rolled steel plate
Optimization.
According to the second aspect of the invention, the invention provides a kind of preparation method of hot rolled steel plate, this method includes：
Slab is heated successively, roughing, finish rolling and solid solution, on the basis of the gross weight of the slab, the slab contains：Fe、
No more than 0.03 weight % C, no more than 0.15 weight % Mn, no more than 0.15 weight % Si, 9-10.3 weight %'s
Ni, 11.5-12.5 weight % Cr, 0.5-0.8 weight % Mo, 0.15-0.25 weight % Ti, no more than 0.2 weight %
Al, no more than 0.2 weight % W, no more than 0.15 weight % V, no more than 0.15 weight % Nb and no more than 0.2 weight
% Cu is measured, is counted using the total deformation rate of roughing and finish rolling as 100%, the deformation rate of the roughing is 60-70%, the finish rolling
The deformation rate of extreme trace time deformation is 8-12%.
In the slab, in addition to above-mentioned element, in addition to the inevitable impurity in addition to silicon.And Fe content
Usually 75-78 weight %.
The present inventor has found in research process, can be changed in obtained hot rolled steel plate using controlled rolling new technology
The morphotropism quantity of austenite so that in elongate crystalline form state austenite structure content account for the 20% of total austenite structure content with
On, obtained hot rolled steel plate has high intensity, high-ductility and while high tenacity with good low temperature and ultralow at normal temperatures
Warm nature energy.
The present invention has no particular limits to the finishing stands, as long as ensureing the deformation rate of finishing stands extreme trace time deformation
For 8-12%.
A preferred embodiment of the invention, the finish rolling includes the deformation of the first passage and the deformation of the second passage,
It is further preferred that being counted using the total deformation rate of roughing and finish rolling as 100%, the deformation rate of the roughing is 60-70%, the essence
The deformation rate for the first passage deformation rolled is 20-30%, and the deformation rate of the second passage deformation of the finish rolling is 8-12%.Using
This can preferred embodiment simplify the production technology of hot rolled steel plate, can further improve the performance of hot rolled steel plate.
A preferred embodiment of the invention, the total deformation rate of the roughing and finish rolling is 70-90%, is preferably
85-90%.The total deformation rate of the roughing and finish rolling is calculated by formula (1)：
The formula (1) of (thickness of slab thickness-finish rolling back plate blank material)/slab thickness × 100%.
There is no particular limitation for thickness of the present invention to the slab, and those skilled in the art can be according to the thickness to finished product
Degree requires to be selected, it is preferable that the thickness of the slab is 70-90% according to the total deformation rate of roughing and finish rolling, preferably
It is determined for 80-85%.
A preferred embodiment of the invention, the thickness of the slab is 20-300mm, preferably 25-130mm.
In the present invention, the heating of plate blank can be carried out on the various conventional devices for heating of plate blank, be used for
The device of heating of plate blank for example can be walking beam furnace.The temperature of the heating of plate blank is preferably 1050-1150 DEG C, enters one
Step is preferably 1090-1110 DEG C.
In the present invention, the roughing can be carried out using the conventional use of roughing mill of those skilled in the art, preferably institute
Roughing is stated for three roller roughing.
A preferred embodiment of the invention, the finishing temperature of the roughing is not less than 850 DEG C, preferably 850-
880℃.Using this kind of preferred embodiment, by controlling the finishing temperature of roughing and the deformation rate of roughing to be more beneficial for raising
Normal temperature performance, cryogenic property and the ultralow temperature performance of hot rolled steel plate.
Air cooling after slab after roughing is handled preferably is rolled, is cooled to after room temperature, clears up surface, pending essence
Roll.
In the present invention, it is preferred to the inlet temperature of the first passage deformation of the finish rolling is 950-1050 DEG C, it is further excellent
Elect 980-1000 DEG C as；It is preferred that the finishing temperature of the first passage deformation of the finish rolling is 830-860 DEG C, more preferably
840-860℃。
In the present invention, it is preferred to which the temperature of the second passage deformation of the finish rolling is 700-780 DEG C, more preferably
720-750℃。
Using preferred embodiment of the present invention, that is, control temperature that the deformation of the first passage and the second passage are deformed and
Deformation rate, is more beneficial for the content of morphotropism in retained austenite in increase gained hot rolled steel plate, meanwhile, it is more favorable to improve
Its normal temperature performance, cryogenic property and ultralow temperature performance.
In the present invention, it is preferred to which the finish rolling is two roller finish rolling.
A preferred embodiment of the invention, after the second passage deformation of finish rolling, rear air cooling is rolled in progress.
A preferred embodiment of the invention, the temperature of the solid solution is 840-860 DEG C, and the time is 0.5-
1.5h.Using this kind of preferred embodiment, it is more beneficial for controlling the content of austenite structure in 5 volume % or so, and have
Beneficial to the performance for improving hot rolled steel plate.
Preferably the rolling method of the invention, by increasing capacitance it is possible to increase the morphotropism quantity of existing retained austenite, realizes hot-rolled steel
Plate volume is strengthened, and improves its yield strength, and ensures that it has preferable low temperature and ultralow temperature performance, to meet new rocket hair
The design use requirement of motivation material.
A preferred embodiment of the invention, the above method also includes：Alkali cleaning, the pickling carried out after the solid solution
And passivation.
The present invention has no particular limits to the condition of the alkali cleaning, pickling and passivation, can be according to the conventional skill in this area
Art means are carried out.
The alkali cleaning can use the NaNO of the NaOH and 20-30 volumes % containing 70-80 volumes %3Alkali lye in alkali crucible
In at 400-420 DEG C alkali cleaning 3-10min, then alkali is exploded off except surface scale in cold water.
The pickling can pass through the H containing 20-30 volumes %2SO4Exist with 1-3 volumes % NaCl acidic aqueous solution
Pickling 10-30 minutes at 75-95 DEG C.The oxide skin for further removing plate surface can be made using the acid cleaning process.
The passivation can use 18-25 volumes % H2SO4With 10-18 volumes % NaNO3The passivation aqueous solution, institute
The temperature for stating passivation can be 40-80 DEG C, and the time of the passivation can be 4-8h.Material can be increased using the passivating process
Expect the ability of surface antirust.
On the other hand, present invention also offers a kind of hot rolled steel plate produced by above-mentioned preparation method.The hot rolled steel plate
Microscopic structure is austenite structure and martensitic structure, and accounting for total austenite structure in the austenite structure content for elongating crystalline form state contains
More than the 20% of amount, yield strength R0.2In more than 785MPa, and subzero 192 DEG C of impact flexibility work(, in more than 78J, grain size is 4
More than level, tensile strength is 930-1000MPa, and elongation percentage is not less than 12%.
At present, it is with the technical requirements of hot rolled steel plate to space flight：Tensile strength is not less than 930MPa；Yield strength R0.2No
Less than 785MPa；Elongation percentage is not less than 12%；Grain size is narrower than 4.0 grades.
By hot rolled steel plate provided by the present invention it can be found that the present invention compared with the technical requirements of space flight hot rolled steel plate
The hot rolled steel plate of offer has while preferable performance at normal temperatures has preferable low temperature and ultralow temperature performance, complies fully with skill
Art requirement.
Present invention also offers application of the above-mentioned hot rolled steel plate in rocket engine.
The present invention is further detailed explanation by the following examples.
In following embodiments and comparative example：
Yield strength R0.2Assay method：GB/T228.1-2010.
Tensile strength RmAssay method：GB/T228.1-2010 metal material tensile testing at ambient temperature.
Elongation percentage A assay method：GB/T228.1-2010 metal material tensile testing at ambient temperature.
The assay method of subzero 192 DEG C of impact flexibility work(：GB/T229-2007.
The assay method of grain size：Comparison method in GB/T 6394-2002.
The assay method of austenite structure and martensitic structure content：X ' pert Pro diffractometers are determined.
In the austenite structure content of elongation crystalline form state by under 100 times of metallographic microscope, being calculated in multiplication factor
Irregular elongation of the length with the length ratio in X-axis not less than 2 in Y-axis being observed that in statistical regions is brilliant
Area ratio shared by kernel structure is obtained.
Embodiment 1-5
The embodiment is used for illustrating the manufacture method for the hot rolled steel plate that the present invention is provided.
Blank obtains slab through conventional forging, and the thickness and various composition of slab are as shown in table 1；Obtained slab is distinguished
Successively carry out heating of plate blank, three roller roughing, air cooling, two roller finish rolling (including first passage deformation and the second passage deformation), air cooling,
Solid solution, alkali cleaning, pickling and passivation, so that hot rolled steel plate is made.Wherein, the temperature of heating of plate blank, the deformation rate of three roller roughing,
Deformation rate, the deformation rate of the second passage deformation, the finishing temperature of roughing, the entrance temperature of the first passage deformation of a time deformation
Degree, the finishing temperature of the first passage deformation, the temperature of the second passage deformation, the temperature of solid solution, the time of solid solution, alkaline cleaning procedure institute
The alkali lye composition that uses, alkali cleaning temperature, alkali cleaning time, composition, pickling temperature, the acid of acidic aqueous solution used in acid cleaning process
Wash the thickness of time, the composition of the used passivation aqueous solution of passivating process, passivation temperature, passivation time and gained hot rolled steel plate
It is as shown in table 2 respectively.The mechanical property of the hot rolled steel plate finally given and the data of microscopic structure are listed in table 3.
The austenite metallographic structure figure of hot rolled steel plate obtained by embodiment 1 is as shown in Figure 1.
Hot rolled steel plate yield strength qualification rate made from method described in 1-5 of the embodiment of the present invention is (higher than industry requirement
785MPa is as qualified) more than 95%.
Comparative example 1
Hot rolled plate is prepared according to the preparation method described in embodiment 1, unlike, the finish rolling only one of which of the operation of rolling
Deformation rate in passage, the operation of rolling is listed in table 2；The austenite metallographic structure figure of obtained hot rolled steel plate is as shown in Figure 2.
Table 1
Table 2
Note：Roughing deformation rate, the first pass deformation rate and the second pass deformation rate are with roughing and total change of finish rolling in table
Form quotient is 100% meter.
Table 3
Can be seen that by the data in table 1-3 can obtain yield strength using preparation method provided by the present invention
R0.2In more than 785MPa, tensile strength RmIn more than 930MPa, elongation percentage A is more than 12%, and grain size is narrower than 4 and met
Under the hot rolled steel plate of Industry code requirements, preferable case, obtained hot rolled steel plate performance is far superior to space flight hot rolled steel plate
Industry requirement, subzero 192 DEG C of impact flexibility work(is in more than 115J, with preferable low temperature and ultralow temperature performance.The present invention is carried
The hot rolled steel plate of confession can be applied in rocket engine completely.
Especially, comparing embodiment 1 and embodiment 4 are it can be found that when solid solubility temperature is more beneficial between 840-860 DEG C
So that austenite structure content reaches minimum in hot rolled steel plate, and complete retain the elongated of austenite crystal in hot rolled steel plate
State, makes hot rolled steel plate mechanical property further improve；Comparative example 1 and embodiment 5 are it can be found that by controlling finishing stands
The deformation temperature of middle extreme trace time, can effectively increase the austenite structure content in elongation crystalline form state, and be conducive to more entering one
Step improves hot rolled steel plate mechanical property；It is can be seen that from embodiment and comparative example by autotelic using two passage finish rolling,
And the deformation rate for controlling the extreme trace time of finish rolling to deform is 8-12%, can provide the hot rolled steel plate for meeting Industry code requirements.
The preferred embodiment of the present invention described in detail above, still, the present invention are not limited in above-mentioned embodiment
Detail, in the range of the technology design of the present invention, a variety of simple variants can be carried out to technical scheme, this
A little simple variants belong to protection scope of the present invention.
It is further to note that each particular technique feature described in above-mentioned embodiment, in not lance
In the case of shield, it can be combined by any suitable means.
In order to avoid unnecessary repetition, the present invention no longer separately illustrates to various possible combinations.
In addition, various embodiments of the present invention can be combined randomly, as long as it is without prejudice to originally
The thought of invention, it should equally be considered as content disclosed in this invention.
Claims (14)
1. a kind of hot rolled steel plate, it is characterised in that on the basis of the gross weight of the hot rolled steel plate, the hot rolled steel plate contains：
Fe, the C for being not more than 0.03 weight %, the Mn for being not more than 0.15 weight %, Si, 9-10.3 weight % for being not more than 0.15 weight %
Ni, 11.5-12.5 weight % Cr, 0.5-0.8 weight % Mo, no more than 0.15-0.25 weight % Ti, 0.2 weight
Measure % Al, no more than 0.2 weight % W, no more than 0.15 weight % V, no more than 0.15 weight % Nb and be not more than
0.2 weight % Cu；The microscopic structure of the hot rolled steel plate be austenite structure and martensitic structure, wherein, in elongate crystalline form
The austenite structure content of state accounts for more than the 20% of total austenite structure content.
2. hot rolled steel plate according to claim 1, wherein, account for total austenite in the austenite structure content for elongating crystalline form state
The 30-40% of tissue content.
3. hot rolled steel plate according to claim 1, wherein, the content of the austenite structure of the hot rolled steel plate is 5-7 bodies
Product %, the content of martensitic structure is 93-95 volumes %.
4. hot rolled steel plate according to claim 1, wherein, the yield strength R of the hot rolled steel plate0.2In more than 785MPa；
Subzero 192 DEG C of impact flexibility work(of the hot rolled steel plate is in more than 78J；The grain size of the hot rolled steel plate is more than 4 grades；Tension
Intensity is 930-1000MPa；Elongation percentage is not less than 12%.
5. hot rolled steel plate according to claim 1, wherein, the yield strength R of the hot rolled steel plate0.2For 790-825MPa；
Subzero 192 DEG C of impact flexibility work(of the hot rolled steel plate is 100-130J；The grain size of the hot rolled steel plate is 5-8 grades；Tension
Intensity is 940-990MPa；Elongation percentage is 12-15.5%.
6. a kind of preparation method of hot rolled steel plate, this method includes：Slab is heated successively, roughing, finish rolling and solid solution, with
On the basis of the gross weight of the slab, the slab contains：Fe, no more than 0.03 weight % C, no more than 0.15 weight %'s
Mn, no more than 0.15 weight % Si, 9-10.3 weight % Ni, 11.5-12.5 weight % Cr, 0.5-0.8 weight %'s
Mo, 0.15-0.25 weight % Ti, no more than 0.2 weight % Al, no more than 0.2 weight % W, no more than 0.15 weight
Measure % V, no more than no more than 0.15 weight % Nb and 0.2 weight % Cu, using the total deformation rate of roughing and finish rolling as
100% meter, the deformation rate of the roughing is 60-70%, and the deformation rate of the extreme trace time deformation of the finish rolling is 8-12%；
The finish rolling includes the deformation of the first passage and the deformation of the second passage；
The total deformation rate of the roughing and finish rolling is 70-90%；
The temperature of the solid solution is 840-860 DEG C, and the time is 0.5-1.5h.
7. preparation method according to claim 6, wherein, counted using the total deformation rate of roughing and finish rolling as 100%, it is described thick
The deformation rate rolled is 60-70%, and the deformation rate of the first passage deformation of the finish rolling is 20-30%, the second of the finish rolling
The deformation rate of secondary deformation is 8-12%.
8. the preparation method according to claim 6 or 7, wherein, the total deformation rate of the roughing and finish rolling is 80-85%.
9. preparation method according to claim 8, wherein, the thickness of the slab is 20-300mm.
10. preparation method according to claim 8, wherein, the thickness of the slab is 25-130mm.
11. preparation method according to claim 7, wherein,
The temperature of the heating is 1050-1150 DEG C；And/or
The finishing temperature of the roughing is not less than 850 DEG C；And/or
The inlet temperature of the first passage deformation of the finish rolling is 950-1050 DEG C；And/or
The finishing temperature of the first passage deformation of the finish rolling is 830-860 DEG C；And/or
The temperature of the second passage deformation of the finish rolling is 700-780 DEG C.
12. preparation method according to claim 11, wherein, the temperature of the heating is 1090-1110 DEG C；And/or
The finishing temperature of the roughing is 850-880 DEG C；And/or
The inlet temperature of the first passage deformation of the finish rolling is 980-1000 DEG C；And/or
The finishing temperature of the first passage deformation of the finish rolling is 840-860 DEG C；And/or
The temperature of the second passage deformation of the finish rolling is 720-750 DEG C.
13. the hot rolled steel plate produced as the preparation method described in any one in claim 6-12.
14. application of the hot rolled steel plate in claim 1-5 and claim 13 described in any one in rocket engine.
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Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SU1165719A1 (en) * | 1983-11-09 | 1985-07-07 | Уральский ордена Трудового Красного Знамени политехнический институт им.С.М.Кирова | Maraging stainless steel |
| CN1708599A (en) * | 2002-11-01 | 2005-12-14 | 山特维克知识产权公司 | Use of a non-corrosive, martensitically hardening steel |
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SU1165719A1 (en) * | 1983-11-09 | 1985-07-07 | Уральский ордена Трудового Красного Знамени политехнический институт им.С.М.Кирова | Maraging stainless steel |
| CN1708599A (en) * | 2002-11-01 | 2005-12-14 | 山特维克知识产权公司 | Use of a non-corrosive, martensitically hardening steel |
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