CN102253045A - Method for evaluating longitudinally-cut low magnification texture quality of high-carbon steel continuous cast square billet - Google Patents
Method for evaluating longitudinally-cut low magnification texture quality of high-carbon steel continuous cast square billet Download PDFInfo
- Publication number
- CN102253045A CN102253045A CN2011100962027A CN201110096202A CN102253045A CN 102253045 A CN102253045 A CN 102253045A CN 2011100962027 A CN2011100962027 A CN 2011100962027A CN 201110096202 A CN201110096202 A CN 201110096202A CN 102253045 A CN102253045 A CN 102253045A
- Authority
- CN
- China
- Prior art keywords
- sample
- segregation
- shaped
- width
- center
- 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
Images
Landscapes
- Investigating And Analyzing Materials By Characteristic Methods (AREA)
Abstract
The invention discloses a method for evaluating the longitudinally-cut low magnification texture quality of a high-carbon steel continuous cast square billet, belongs to a method for judging the defect level of a metal material texture and aims to provide a method for reflecting the segregation defect condition of a continuous cast square billet part more correctly and completely, and judging the defect level of the low magnification texture of the continuous cast square billet according to the defect. The method comprises the following steps of: longitudinally cutting a continuous cast billet manufacturing sample along the axis line, comparing the sample and the V-shaped texturing width, V-shaped texturing number, V-shaped texturing color, and central segregation straight texturing length of a reference map, and judging the degree of the V-shaped segregation and the central segregation of the sample low magnification texture. The method is small in working amount and high in efficiency and is an ideal method for evaluating the longitudinally-cut low magnification texture quality of the high-carbon steel continuous cast square billet.
Description
Technical field: the present invention relates to a kind of method of judging the metal material tissue defect level, relate in particular to a kind of judgement Cast High-Carbon Steel Billet macrostructure V-shaped segregation degree and center segregation degree methods.
Background technology: well-known, because the singularity of high-carbon steel continuous casting process, tend to core in Cast High-Carbon Steel Billet and periodically produce defectives such as shrinkage cavity, loose, segregation vertically, and these defectives can cause producing cup-and-cone columnar fracture with the rolling wire rod of Cast High-Carbon Steel Billet in drawing process, influence the drawing property of product and the properties of product after the drawing.Tradition macroscopic examination method is only at sample of the transversal section, steel billet upper edge of needs check intercepting, adopt GB2269-91 " macrostructure of steel and defective acid etching method of inspection " that sample is handled then, and then " carbon constructional quality steel and structural alloy steel continuous casting square billet macrostructure defective are graded and schemed ", YB4002-91 " continuous casting square billet macrostructure defective grading figure " evaluate to contrast YB/T153-1999 respectively.Because defectives such as the shrinkage cavity of Cast High-Carbon Steel Billet core, loose, segregation distribute along continuous casting square billet is axially interrupted, therefore this traditional analytic approach can not reflect the state of Cast High-Carbon Steel Billet core tissue defects objective, comprehensively, especially can not reflect V-shaped segregation and center segregation, more can not judge V-shaped segregation and center segregation defect level; Need badly and a kind ofly can reflect continuous casting square billet core segregation defective pattern more accurately, all sidedly, and the method for the good and bad situation of pattern continuous casting square billet macrostructure being judged according to this defective.
Summary of the invention: in order to overcome the defective that exists in the prior art, the present invention aims to provide a kind of evaluation Cast High-Carbon Steel Billet vertical profile macrostructure method for quality, this method can reflect continuous casting square billet core segregation defective pattern comparatively accurately, all sidedly, and according to this defective pattern continuous casting square billet macrostructure defect level is judged.
To achieve these goals, the present invention is by the following technical solutions: along solidifying the continuous casting square billet of center line longitudinally cutting length for 1.5 times of self width, behind machining and acid etching, make sample then, with this sample contrast the V-shaped segregation reference map respectively, the center segregation reference map compares judgement by the following method:
1) if the V font texture width of sample less than the V font texture width of V-shaped segregation reference map, shows that then the V-shaped segregation degree of sample is lighter; Otherwise, show that then the V-shaped segregation degree of sample is more serious; If the V font texture width of sample equals the V font texture width of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is suitable with the benchmark rank;
2) if the V font texture quantity of sample is less than the V font texture quantity of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is lighter; Otherwise, show that then the V-shaped segregation degree of sample is more serious; If the V font texture quantity of sample equals the V font texture quantity of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is suitable with the benchmark rank;
3) if the V font texture color of sample is more shallow than the V font texture color of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is lighter; Otherwise, show that then the V-shaped segregation degree of sample is more serious; If the V font texture color of sample is identical with the V font texture color of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is suitable with the benchmark rank;
4) the V-shaped segregation width=solid rate that solidifies the center when sample is the liquid core width at 0.1～0.2 place, and when the V font quantity of V-shaped segregation equals the V-shaped segregation reference map, if " 1 " font texture length of sample center segregation shows then that less than " 1 " font texture length of center segregation reference map the center segregation degree of sample is lighter; Otherwise, show that then the center segregation degree of sample is more serious; If " 1 " font texture length of sample center segregation equals " 1 " font texture length of center segregation reference map, show that then the center segregation degree of sample is suitable with the benchmark rank; If " 1 " font texture width of sample center segregation shows then that less than " 1 " font texture width of center segregation reference map sample center segregation degree is lighter; Otherwise, show that then sample center segregation degree is more serious; If " 1 " font texture width of sample center segregation equals " 1 " font texture width of center segregation reference map, show that then sample center segregation degree is suitable with the benchmark rank;
The magnetic stirrer operate as normal time institute intercepted length that described V-shaped segregation reference map is meant crystallizer is the strand of 1.5 times of self width, then along solidifying this strand of center line longitudinally cutting, and, be that the liquid core width at 0.1～0.2 place is chosen the photo that the benchmark sample production gets by the width=1 * solid rate of V-shaped segregation again through machining and acid etching;
The magnetic stirrer operate as normal time institute intercepted length that described center segregation reference map is meant crystallizer is the strand of 1.5 times of self width, then along solidifying this strand of center line longitudinally cutting, and, be that the standard of the liquid core width at 0.1～0.2 place is chosen the photo that the benchmark sample production of center segregation line length=2 * minimum solidification shrinkage shrinkage cavity spacing gets by the width=1 * solid rate of V font texture again through machining and acid etching.
In general, the continuous casting billet macrostructure is broadly divided into three kinds of situations: all be column crystal except that chill zone, part is that column crystal, part are equiax crystal, all equiax crystal (see figure 3); For high-carbon steel, mainly be the second class situation, high-carbon steel continuous casting base segregation defective forming process is as follows.
In the casting process of high-carbon steel, the liquidus temperature of establishing molten steel is T
L, solidus temperature is T
S, when temperature is the molten steel of T when watering into crystallizer, molten steel generates a chill and initial solidification shell at crystallizer wall, simultaneously the temperature of molten steel since heat conduction and convection current begin to descend.Along with the base shell is drawn out crystallizer, the steel billet that secondary cooling water contains the liquid core to the center is lowered the temperature, and base shell inside surface column crystal begins growth, and the liquid steel temperature of liquid in-core continues to descend.Along with the decline of liquid steel temperature in the base shell, the molten steel outburst forms nuclei of crystallization (see figure 4) in the base shell when the degree of supercooling of molten steel acquires a certain degree.Because molten steel density is less than the density of steel, the nuclei of crystallization that outburst forms in molten steel, sinks and grow up, the nuclei of crystallization are piled up formation steel billet center then equiax crystal district.The nuclei of crystallization in equiax crystal district are grown up in dropping process and are formed tree skill shape, and the different nuclei of crystallization are piled up mutually, have formed bigger space owing to the crystal grain branch supports mutually between the nuclei of crystallization and the nuclei of crystallization; Filled up molten steel between this space.The continuous decline of and steel billet temperature descending along with steel billet, the molten steel in equiax crystal district begins to solidify.Because molten steel density is littler than steel density, 3～4% contraction takes place in molten steel volume in process of setting; And the molten steel on top is because mutual the stopping to nourish to the contraction of bottom and fill of the equiax crystal nuclei of crystallization that support, thus the strand SMIS can be regularly or the scope of measured length form shrinkage cavity.When the dendrite interval in equiax crystal district was big, the solidification shrinkage of strand bottom can be replenished by interdendritic remaining molten steel.Because casting billet surface has the thermograde of existence to SMIS, the molten steel of mobile feeding can form one downward " arrow " and shape flow channel (see figure 7).
The liquidus temperature of molten steel and the difference of solidus temperature mainly cause owing to alloying element.In the molten steel solidification process, the molten steel that does not contain or contain less alloying element solidifies in advance, is rich in the molten steel after coagulation of alloying element; Thereby the mobile arrow-shaped flow channel that forms of feeding has just formed a line of segragation that is " arrow " shape.The formed V font of the two arms texture of arrow-shaped flow channel is a V-shaped segregation, and the center of arrow-shaped flow channel formed " 1 " font texture is called center segregation, and the hole that forms because of the MOLTEN STEEL FLOW of final set is a center porosity.If the dendrite interval in equiax crystal district is excessive, perhaps improper because of the cooling water distribution, the MOLTEN STEEL FLOW at arrow-shaped flow channel center can form a pipeline, is called central pipe; It is different from the shrinkage cavity (see figure 7) that forms because of solidification shrinkage.Described five defective part can individualism, also can exist simultaneously.
For mild carbon steel, because liquidus temperature T
LWith solidus temperature T
SBetween the temperature difference little, along with the decline of steel billet temperature, interdendritic molten steel solidifies very soon, has little time to flow, thereby does not form or few " arrow " v shaped segregation and loose (see figure 6) of forming.For medium carbon steel, because liquidus temperature T
LWith solidus temperature T
SBetween the temperature difference bigger, along with the decline of steel billet temperature, interdendritic molten steel can not solidify very soon, thereby can form " arrow " v shaped segregation and loose.For high-carbon steel, because liquidus temperature T
LWith solidus temperature T
SBetween the temperature difference much bigger than mild carbon steel and medium carbon steel, along with the decline of steel billet temperature, interdendritic molten steel can not solidify very soon, thereby can form huge " arrow " v shaped segregation and loose.In order to eliminate V-shaped segregation, normal dynamic crystal grain thinning method, the i.e. electromagnetic agitation of adopting in the production.To medium carbon steel, often use one section electromagnetic agitation (MEMS).For high-carbon steel, often use two sections electromagnetic agitation (MEMS+FEMS).At present industry is normal adopts one section or two sections electromagnetic stirring methods to produce the high-carbon continuous casting billets, so this method is made an appraisal to the segregation defective of the continuous casting billet of one section or two sections electromagnetic stirring method production.Learn by research molten steel solid rate and MOLTEN STEEL FLOW sexual intercourse: on the conticaster of crystallizer electromagnetic agitation operate as normal, after steel billet is drawn out crystallizer, column crystal on the base shell is evenly grown, long column crystal is fractureed by the steel stream of central motion and sneaks into the steel stream of motion, becomes the nucleating center of equiax crystal; When steel billet when to drop to the molten steel solid rate be 0.1 position, the basic stop motion of the molten steel of SMIS, but molten steel still has flowability; As long as at solid rate is that 0.1 place begins to stir, even be that 0.4 o'clock molten steel still can stir to solid rate; If stop this moment stirring, the molten steel motion stops immediately.When solid rate reaches after 0.6, no matter molten steel is stirred with great mixing power.And after the motion of center molten steel stopped, the even growth of column crystal also stopped, and the molten steel at center changes static freezing over to; The dendritic equiax crystal of center tree supports mutually, causes the top molten steel to replenish the bottom solidification shrinkage, and solidification shrinkage is mainly replenished by the interdendritic MOLTEN STEEL FLOW of equiax crystal.As previously mentioned, the liquidus temperature T of high-carbon steel molten steel
LWith solidus temperature T
SBetween the temperature difference bigger, the molten steel composition difference of molten steel that solidifies earlier and final set is big, space, equiax crystal interdendritic is bigger, molten steel replenishes solidification shrinkage along the dendrite Clearance Flow; Under the thermograde effect of the continuous casting billet in process of setting, the molten steel that flows forms a V-shaped segregation, by research that V-shaped segregation is formed as can be known, we can determine the heavy degree of coming of V-shaped segregation by the width of V-shaped segregation, and can be the index of the liquid core width at 0.1～0.2 place as a scale weighing the segregation of V font with solid rate.According to the central idea of solidification end electromagnetic agitation, the solidified structure of solidification end should be fine and close wide and thin equiax crystal.Therefore, when flow in the equiax crystal district of same width generation equiax crystal interdendritic, because the cooling water distribution is different with the equiax crystal dendrite interval, interdendritic, equiax crystal district molten steel flow ability is also different.Be reflected on the low power picture and be: original grain is big, the V-shaped segregation pipeline on the equal length direction many (V font texture is many); Original grain is little, the V-shaped segregation pipeline on the equal length direction few (V font texture is few).According to the quantity of V-type segregation on the unit length, we can determine the high-carbon steel continuous casting base in casting cycle, the height situation of molten steel overheat.According to aforementioned analysis as can be seen, under identical cooling degree situation, the solid-liquid phase temperature difference is big more, and equiax crystal interdendritic molten steel flow ability is also strong more; But when the solid-liquid phase temperature difference is identical, cool off by force more, equiax crystal interdendritic molten steel flow is weak more.This is reflected in the macroscopic examination and shows as: cooling power was strong more when end solidified, and the V-shaped segregation color is shallow more.
In the process of setting of continuous casting billet since molten steel solidification shrink can intermittent generation shrinkage cavity, this intermittently distance be 5cm～10cm approximately.Generation place center segregation in shrinkage cavity can compile, and advances the performance of face harm steel, and therefore the minimum spacing 5cm that shrinkage cavity can be taken place defines the order of severity of center segregation as a standard foundation of evaluation center segregation according to this standard.Simultaneously, according to the order of severity of V-shaped segregation, we can judge that the molten steel that is rich in alloying element what are arranged has taken place to flow to the center, and are pooled to shrinkage cavity place by the center segregation passage, and then the harm performance, therefore with the order of severity of V-shaped segregation index as another assessment centers segregation.
From aforementioned analysis as can be seen, under identical cooling degree situation, the solid-liquid phase temperature difference is big more, and equiax crystal interdendritic molten steel flow ability is also strong more, but when the solid-liquid phase temperature difference is identical, cools off by force more, and equiax crystal interdendritic molten steel flow is weak more.This is reflected in the macroscopic examination and shows as: cooling power was strong more when end solidified, and the center segregation color is shallow more.
Compared with the prior art, the present invention is owing to adopted technique scheme, solidified the intercepting of center line longitudinally cutting with originally having changed into along continuous casting square billet by the method for transversal section intercepting sample, behind machining and acid etching, make sample, therefore not only can make the V-shaped segregation defective, the center segregation defective that are present in continuous casting square billet core tissue be able to comprehensive, objective, appear clearly, thereby can judge the defect level of continuous casting square billet macrostructure existence; And workload is little, efficient is high.
Description of drawings:
Fig. 1 adopts the inventive method to appear along Cast High-Carbon Steel Billet to solidify the V-shaped segregation figure that center line distributes;
Fig. 2 adopts the inventive method to appear along Cast High-Carbon Steel Billet to solidify center line center of distribution segregation map;
Several synoptic diagram of organizing that may have in Fig. 3 foundry goods;
Fig. 4 is that the relation of nucleation rate and growth rate and degree of supercooling is seen figure;
Fig. 5 is a dendrite growth synoptic diagram;
Fig. 6 does not have the continuous casting billet core of segregation defective to organize synoptic diagram;
Fig. 7 exists the continuous casting billet core of segregation defective to organize synoptic diagram.
Embodiment: the invention will be further described below in conjunction with accompanying drawing and specific embodiment:
Along solidifying the continuous casting square billet of center line longitudinally cutting length for 1.5 times of self width, behind machining and acid etching, make sample then, with this sample contrast the V-shaped segregation reference map respectively, the center segregation reference map compares judgement by the following method:
1) as shown in Figure 1: if the V font texture width of sample shows then that less than the V font texture width of V-shaped segregation reference map the V-shaped segregation degree of sample is lighter; Otherwise, show that then the V-shaped segregation degree of sample is more serious; If the V font texture width of sample equals the V font texture width of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is suitable with the benchmark rank;
2) as shown in Figure 1:, show that then the V-shaped segregation degree of sample is lighter if the V font texture quantity of sample is less than the V font texture quantity of V-shaped segregation reference map; Otherwise, show that then the V-shaped segregation degree of sample is more serious; If the V font texture quantity of sample equals the V font texture quantity of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is suitable with the benchmark rank;
3) as shown in Figure 1:, show that then the V-shaped segregation degree of sample is lighter if the V font texture color of sample is more shallow than the V font texture color of V-shaped segregation reference map; Otherwise, show that then the V-shaped segregation degree of sample is more serious; If the V font texture color of sample is identical with the V font texture color of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is suitable with the benchmark rank;
4) as shown in Figure 2: the V-shaped segregation width=solid rate that solidifies the center when sample is the liquid core width at 0.1～0.2 place, and when the V font quantity of V-shaped segregation equals the V-shaped segregation reference map, if " 1 " font texture length of sample center segregation shows then that less than " 1 " font texture length of center segregation reference map sample center segregation degree is lighter; Otherwise, show that then sample center segregation degree is more serious; If " 1 " font texture length of the center segregation of sample equals " 1 " font texture length of center segregation reference map, show that then sample center segregation degree is suitable with the benchmark rank; If " 1 " font texture width of sample center segregation shows then that less than " 1 " font texture width of center segregation reference map sample center segregation degree is lighter; Otherwise, show that then sample center segregation degree is more serious; If " 1 " font texture width of sample center segregation equals center segregation " 1 " the font texture width of center segregation reference map, show that then sample center segregation degree is suitable with the benchmark rank.
The magnetic stirrer operate as normal time institute intercepted length that described V-shaped segregation reference map is meant crystallizer is the strand of 1.5 times of self width, then along solidifying this strand of center line longitudinally cutting, and, be that the liquid core width at 0.1～0.2 place is chosen the photo that the benchmark sample production gets by the width=1 * solid rate of V-shaped segregation again through machining and acid etching;
The magnetic stirrer operate as normal time institute intercepted length that described center segregation reference map is meant crystallizer is the strand of 1.5 times of self width, then along solidifying this strand of center line longitudinally cutting, and, be that the standard of the liquid core width at 0.1～0.2 place is chosen the photo that the benchmark sample production of center segregation line length=2 * minimum solidification shrinkage shrinkage cavity spacing gets by the width=1 * solid rate of V font texture again through machining and acid etching;
Wherein, solid rate is that the liquid core width at 0.1～0.2 place can be calculated as follows:
L0.1＝2R×(1-D
s)
L0.1---for strand solid rate in process of setting is the liquid core width (mm) at 0.1～0.2 place;
D
s---solidification rate, D
s=0.7;
R---casting blank section radius (mm);
Minimum solidification shrinkage shrinkage cavity spacing=5cm.
In the above-mentioned example, the sample production method is as follows:
1) cutting plane solidifies the center by continuous casting square billet in order to guarantee, should carry out vertical profile according to cross-sectional central pipe or center porosity position to steel billet then at first to the cross-sectional macroscopic examination of carrying out of steel billet;
2) along solidifying the sample of longitudinally cutting one segment length in center, stay process redundancy 5 ± 2.5mm for 1.5 times of himself width;
3) the longitudinally cutting face to sample carries out metal cutting processing, and assurance machined surface distance is solidified the distance≤3mm of center line, the roughness≤1.6 μ m of assurance machined surface;
4) greasy dirt of removal machined surface;
5) machined surface of sample is edge-on and be immersed in 65～80 ℃ the aqueous hydrochloric acid solution and corrode, until the machined surface of sample lose metallic luster and clear manifest the segregation line till; Described hydrochloric acid solution is formulated by 1: 1 volume by technical hydrochloric acid and water;
5) sample is pulled out be immersed in immediately and soaked 3～10 minutes in the buck, in buck, remove corrosion thing simultaneously attached to the sample machined surface;
6) sample pulled out immediately with cold water flush, used the hot water injection more than 80 ℃ clean again, then sample is erect by the V font line mode that Open Side Down, tip makes progress, the machined surface with sample dries up from top to bottom.
Claims (1)
1. evaluate Cast High-Carbon Steel Billet vertical profile macrostructure method for quality for one kind, it is characterized in that: along solidifying the continuous casting square billet of center line longitudinally cutting length for 1.5 times of self width, behind machining and acid etching, make sample then, with this sample contrast the V-shaped segregation reference map respectively, the center segregation reference map compares judgement by the following method:
1) if the V font texture width of sample less than the V font texture width of V-shaped segregation reference map, shows that then the V-shaped segregation degree of sample is lighter; Otherwise, show that then the V-shaped segregation degree of sample is more serious; If the V font texture width of sample equals the V font texture width of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is suitable with the benchmark rank;
2) if the V font texture quantity of sample is less than the V font texture quantity of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is lighter; Otherwise, show that then the V-shaped segregation degree of sample is more serious; If the V font texture quantity of sample equals the V font texture quantity of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is suitable with the benchmark rank;
3) if the V font texture color of sample is more shallow than the V font texture color of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is lighter; Otherwise, show that then the V-shaped segregation degree of sample is more serious; If the V font texture color of sample is identical with the V font texture color of V-shaped segregation reference map, show that then the V-shaped segregation degree of sample is suitable with the benchmark rank;
4) the V-shaped segregation width=solid rate that solidifies the center when sample is the liquid core width at 0.1～0.2 place, and when the V font quantity of V-shaped segregation equals the V-shaped segregation reference map, if " 1 " font texture length of sample center segregation shows then that less than " 1 " font texture length of center segregation reference map the center segregation degree of sample is lighter; Otherwise, show that then the center segregation degree of sample is more serious; If " 1 " font texture length of sample center segregation equals " 1 " font texture length of center segregation reference map, show that then the center segregation degree of sample is suitable with the benchmark rank; If " 1 " font texture width of sample center segregation shows then that less than " 1 " font texture width of center segregation reference map sample center segregation degree is lighter; Otherwise, show that then sample center segregation degree is more serious; If " 1 " font texture width of sample center segregation equals " 1 " font texture width of center segregation reference map, show that then sample center segregation degree is suitable with the benchmark rank;
The magnetic stirrer operate as normal time institute intercepted length that described V-shaped segregation reference map is meant crystallizer is the strand of 1.5 times of self width, then along solidifying this strand of center line longitudinally cutting, and, be that the liquid core width at 0.1～0.2 place is chosen the photo that the benchmark sample production gets by the width=1 * solid rate of V-shaped segregation again through machining and acid etching;
The magnetic stirrer operate as normal time institute intercepted length that described center segregation reference map is meant crystallizer is the strand of 1.5 times of self width, then along solidifying this strand of center line longitudinally cutting, and, be that the standard of the liquid core width at 0.1～0.2 place is chosen the photo that the benchmark sample production of center segregation line length=2 * minimum solidification shrinkage shrinkage cavity spacing gets by the width=1 * solid rate of V font texture again through machining and acid etching.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2011100962027A CN102253045A (en) | 2011-04-18 | 2011-04-18 | Method for evaluating longitudinally-cut low magnification texture quality of high-carbon steel continuous cast square billet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2011100962027A CN102253045A (en) | 2011-04-18 | 2011-04-18 | Method for evaluating longitudinally-cut low magnification texture quality of high-carbon steel continuous cast square billet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN102253045A true CN102253045A (en) | 2011-11-23 |
Family
ID=44980435
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2011100962027A Pending CN102253045A (en) | 2011-04-18 | 2011-04-18 | Method for evaluating longitudinally-cut low magnification texture quality of high-carbon steel continuous cast square billet |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102253045A (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103091335A (en) * | 2013-01-25 | 2013-05-08 | 湖北汽车工业学院 | Method for testing crack sensitivity of precision steel casting and test model thereof |
| CN105158046A (en) * | 2015-06-30 | 2015-12-16 | 江苏联峰能源装备有限公司 | Rapid preparation method of continuous casting billet macro-sample |
| CN105352966A (en) * | 2015-09-29 | 2016-02-24 | 邢台钢铁有限责任公司 | High carbon steel continuous casting billet internal quality inspection method |
| CN105716929A (en) * | 2016-03-04 | 2016-06-29 | 攀钢集团攀枝花钢铁研究院有限公司 | Quantitative assessment method for continuous casting central pipe |
| CN107367510A (en) * | 2016-05-12 | 2017-11-21 | 鞍钢股份有限公司 | Method for measuring isometric crystal rate of high-carbon steel continuous casting billet |
| CN109035221A (en) * | 2018-07-10 | 2018-12-18 | 成都先进金属材料产业技术研究院有限公司 | Macrostructure intelligence ranking method based on image recognition depth learning technology |
| CN111537691A (en) * | 2020-04-27 | 2020-08-14 | 江苏省沙钢钢铁研究院有限公司 | Square billet center macrosegregation analysis method |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1259663A (en) * | 1999-12-28 | 2000-07-12 | 上海宝钢集团公司 | Automatic evaluation method of casting ingot cross section quality |
| KR20030055946A (en) * | 2001-12-27 | 2003-07-04 | 주식회사 포스코 | A method for evaluating surface pop-up defect on a galvanized steel sheet |
-
2011
- 2011-04-18 CN CN2011100962027A patent/CN102253045A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1259663A (en) * | 1999-12-28 | 2000-07-12 | 上海宝钢集团公司 | Automatic evaluation method of casting ingot cross section quality |
| KR20030055946A (en) * | 2001-12-27 | 2003-07-04 | 주식회사 포스코 | A method for evaluating surface pop-up defect on a galvanized steel sheet |
Non-Patent Citations (1)
| Title |
|---|
| 魏果能等: "连铸和模铸轴承钢的冶金质量及接触疲劳寿命", 《特殊钢》 * |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103091335A (en) * | 2013-01-25 | 2013-05-08 | 湖北汽车工业学院 | Method for testing crack sensitivity of precision steel casting and test model thereof |
| CN103091335B (en) * | 2013-01-25 | 2015-04-08 | 湖北汽车工业学院 | Method for testing crack sensitivity of precision steel casting and test model thereof |
| CN105158046A (en) * | 2015-06-30 | 2015-12-16 | 江苏联峰能源装备有限公司 | Rapid preparation method of continuous casting billet macro-sample |
| CN105158046B (en) * | 2015-06-30 | 2018-01-16 | 江苏联峰能源装备有限公司 | A kind of fast preparation method of continuous casting billet low power sample |
| CN105352966A (en) * | 2015-09-29 | 2016-02-24 | 邢台钢铁有限责任公司 | High carbon steel continuous casting billet internal quality inspection method |
| CN105352966B (en) * | 2015-09-29 | 2019-04-16 | 邢台钢铁有限责任公司 | A kind of method of inspection of strand casted from high carbon steel internal soundness |
| CN105716929A (en) * | 2016-03-04 | 2016-06-29 | 攀钢集团攀枝花钢铁研究院有限公司 | Quantitative assessment method for continuous casting central pipe |
| CN107367510A (en) * | 2016-05-12 | 2017-11-21 | 鞍钢股份有限公司 | Method for measuring isometric crystal rate of high-carbon steel continuous casting billet |
| CN109035221A (en) * | 2018-07-10 | 2018-12-18 | 成都先进金属材料产业技术研究院有限公司 | Macrostructure intelligence ranking method based on image recognition depth learning technology |
| CN111537691A (en) * | 2020-04-27 | 2020-08-14 | 江苏省沙钢钢铁研究院有限公司 | Square billet center macrosegregation analysis method |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102253045A (en) | Method for evaluating longitudinally-cut low magnification texture quality of high-carbon steel continuous cast square billet | |
| Lee et al. | Modeling microporosity in aluminum–silicon alloys: a review | |
| Eskin et al. | Structure formation and macrosegregation under different process conditions during DC casting | |
| CN108624959B (en) | Method for preparing single crystal superalloy using solution treated seed crystal | |
| RU2720414C2 (en) | Optimization of liquid metal flow during casting into crystalliser by direct cooling | |
| Hong et al. | Geometrical effect of freckle formation on directionally solidified superalloy CM247 LC components | |
| Li et al. | Effect of solidification conditions and surface pores on the microstructure and columnar-to-equiaxed transition in solidification under microgravity | |
| CN112185472B (en) | Method for predicting freckle morphology defects in paste-like region of directional solidification peritectic alloy | |
| Fu et al. | Microstructure evolution in AISI 304 stainless steel during near rapid directional solidification | |
| Yao et al. | Effect of steel strip feeding on the columnar-equiaxed solidification in a large continuous casting round bloom | |
| Yan et al. | Numerical simulation of dendrite growth in Ni-based superalloy casting during directional solidification process | |
| Salgado-Ordorica et al. | Morphology and growth kinetic advantage of quenched twinned dendrites in Al-Zn alloys | |
| Bing et al. | Hot cracking tendency test and simulation of 7075 semi-solid aluminium alloy | |
| Silva et al. | The columnar to equiaxed transition during the horizontal directional solidification of Sn–Pb alloys | |
| CN101773992A (en) | Electromagnetic stirring low liquid level casting method for aluminum alloy slab ingot | |
| CN116460258A (en) | Application method of traveling wave linear electromagnetic stirrer for controlling V-shaped segregation of square and round billets | |
| Xu et al. | Effect of competitive crystal growth on microstructural characteristics of directionally solidified nickel-based single crystal superalloy | |
| Beckermann | Macrosegregation | |
| Chen et al. | Formation of twinned dendrites during unidirectional solidification of Al-32% Zn alloy | |
| Hernando et al. | An overview of isothermal coarsening in hypoeutectic lamellar cast iron | |
| Yuan et al. | Study on the homogeneity of tilted dendritic structures in single crystal superalloys | |
| Kao et al. | The role of the pressure index in porosity formation in A356 alloy castings | |
| Kuo | Mechanical properties and porosity content of A201 aluminum alloy castings in different cooling rate sand molds | |
| JP6829373B2 (en) | Manufacturing method of porous structure | |
| CN110382136A (en) | The crystal grain refinement of the ingot casting of shear-induced |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C02 | Deemed withdrawal of patent application after publication (patent law 2001) | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Application publication date: 20111123 |