G. YUAN et al.: FABRICATION AND PROPERTIES OF HIGH-CHROMIUM CAST IRON DISPERSED STEEL ...
349–356
FABRICATION AND PROPERTIES OF HIGH-CHROMIUM CAST
IRON DISPERSED STEEL MATRIX COMPOSITE
IZDELAVA IN LASTNOSTI LITINE Z VISOKO VSEBNOSTJO
KROMA DISPERGIRANE V JEKLENI KOMPOZITNI MATRICI
Guofeng Yuan
*
, He Wang, Xiuli Guo, Fei Zhao, Chengqi Yan, Han He
School of Mechanical Engineering, Anyang Institute of Technology, Anyang 455000, China
Prejem rokopisa – received: 2024-02-17; sprejem za objavo – accepted for publication: 2024-04-10
doi:10.17222/mit.2024.1111
Composites with high-chromium cast iron (HCCI) dispersed in a steel matrix were prepared using the multilayer rolling-form-
ing method. The macroscopic morphology, microstructure and tensile properties of the bimetal composites were analyzed. The
experimental results showed that brittle HCCI layers were necked and broken into uneven blocks or granules after hot-rolling
forming. The fractured HCCI was encased in carbon steel completely, and the two metals achieved good metallurgical bonding.
The Fe, Cr, Mn and C elements were diffused at the interface. The tensile strength of the composite was better than that of the
as-cast iron. During the process of tensile deformation, the composite displayed a complex crack propagation rather than a frac-
ture caused directly by brittleness. The damage tolerance and energy absorption capacity of the bimetallic composite were im-
proved with a decentralized structure.
Keywords: hot rolling, high-chromium cast iron, dispersed, microstructure
Avtorji v ~lanku opisujejo pripravo in karakterizacijo kompozitov jeklene litine z visoko vsebnostjo kroma (HCCI), ki je
enakomerno porazdeljena (dispergirana) v jekleni matrici z nizko vsebnostjo ogljika (LCS; low carbon steel). Materiale so
pripravili s postopkom oblikovanja z ve~plastnim valjanjem. Sledila je makroskopska analiza morfologije, mikrostrukture in
nateznih lastnosti bimetalnih kompozitov. Eksperimentalni rezultati so pokazali, da so bile po vro~em valjanju krhke HCCI
plastistanj{ane in nalomljene znotraj neravnih blokov ali granul. Prelom HCCI je bilpopolnoma obdan z LCS in obe kovini sta
se med seboj dobro metalur{ko povezali. Elementi Fe, Cr, Mn in C so medsebojno difundirali na meji obeh kovin. Natezna
trdnost kompozita je bila bolj{a od natezne trdnosti jeklene litine. Med procesom natezne deformacije kompozita je prednostno
pri{lo do kompleksnega procesa napredovanja razpok in manj kot posledica krhkega loma. Avtorji v zaklju~kih ugotavljajo, da
sta bili odpornost na po{kodbe in kapaciteta absorpcijske energije bimetalnega kompozita izbolj{ani zaradi decentralizacije
strukture.
Klju~ne besede: vro~e valjanje; jeklena litina z visoko vsebnostjo kroma;dispergiranost; mikrostruktura
1 INTRODUCTION
Wear-resistant materials have broad application pros-
pects in modern engineering fields, such as mining, met-
allurgy, coal and transportation. Wear resistant parts of-
ten require good wear resistance and impact toughness
during service.
1–3
High-chromium cast iron (HCCI), as a
widely used wear-resistant material, has high hardness
and excellent wear resistance. However, because of its
poor impact toughness, HCCI fractures easily under im-
pact fracture in engineering applications.
4–6
In order to improve the comprehensive mechanical
properties of HCCI, scholars often use the methods of
micro-alloying, semi-solid forming, electric-pulse treat-
ment, thermoplastic deformation and heat treatment to
improve or refine the carbide in HCCI.
7–10
In addition, re-
search on wear-resistant composite materials has been
carried out. Composite materials of solid HCCI and duc-
tile low-carbon steel (LCS) have good resistance to im-
pact and wear as they effectively combine the advantages
of the two metals, having an important application value
in engineering.
At present, scientists often use duo-casting, surface
compounding, diffusion bonding, casting and hot rolling
to prepare HCCI/LCS bimetallic composites. Javaheri et
al. prepared carbon steel and HCCI bimetallic composite
materials with the liquid-solid casting bonding method.
11
They found that the elongation and impact toughness of
the bimetal were lower than those of LCS and better than
those of a single HCCI plate. Jilleh et al. studied the
microstructure evolution of an HCCI surface welding
layer, in which Nb and Mo were used as the main addi-
tives, while W and V were used as the secondary addi-
tives during the solidification process. The results
showed that adding alloying elements helped refine the
M
7
C
3
carbide in HCCI.
12
Eroglu and Kurt successfully
prepared HCCI/LCS composite materials through the hot
pressure diffusion method. It was found that under a cer-
tain pressure (8 MPa), the bonding strength of the inter-
face between the two metals was improved by increasing
the diffusion temperature or time.
13
Xie et al. produced a
sandwich-structured LCS/HCCI/LCS composite slab by
casting, which was then subjected to multi-pass hot-roll-
Materiali in tehnologije / Materials and technology 58 (2024) 3, 349–356 349
UDK 669.1:621.771.8 ISSN 1580-2949
Original scientific article/Izvirni znanstveni ~lanek MTAEC9, 58(3)349(2024)
*Corresponding author's e-mail:
aygxyygf@163.com (Guofeng Yuan)

ing deformation. They analyzed the microstructure of the
interface between the two metals and discussed the influ-
ence of different heat-treatment processes on the
microstructure.
14,15
In recent years, accumulative
roll-bonding (ARB) technology, or multilayer rolling
technology, has been favored by many scientists in the
preparation of layered composites.
16–18
In the rolling
forming process of bimetal multilayers, the two metals
undergo plastic deformation together, finally producing a
layered composite with a multilayer structure. However,
if the mechanical properties of the two metals are differ-
ent or the cumulative deformation is large, the harder
layer will be necked and fractured with an increase in the
strain or stress, forming granules or sheets which will be
dispersed in the softer layer. At present, there are few
studies on the preparation of HCCI/LCS composites with
multilayer or cumulative rolling.
On the basis of the previous research, HCCI-dis-
persed composites were prepared by hot-rolling forming
in this study. The macrostructure, microstructure and
tensile properties of the composites were analyzed. The
results provide a foundation and reference for the study
of HCCI/LCS composites.
2 MATERIALS AND METHODS
2.1 Materials
As-received materials used in this study were
2.5 mm-thick as-cast HCCI sheets and 1 mm-, 2 mm-
and 3 mm-thick commercial LCS sheets. Both HCCI and
LCS sheets were cut into samples of (150 × 100) mm.
The chemical compositions of HCCI and LCS are pro-
vided in Table 1.
Table 1: Chemical compositions (w/%) of HCCI and LCS
Material C Si Cr Mn P S Mo Ni Fe
HCCI 2.8 1.1 28 1.0 0.02 0.02 0.5 0.4 balance
LCS 0.12 0.2 0.1 0.5 0.01 0.002 / / balance
Figure 1 shows a scanning electron microscope
(SEM) microgram of the as-cast iron. A high volume
fraction of hard (Fe,Cr)
7
C
3
carbides was distributed in
the matrix of HCCI, contributing to excellent wear resis-
tance while greatly reducing the workability of HCCI.
2.2 Hot-rolling forming
In the present study, three kinds of slabs with differ-
ent volume ratios were prepared, labeled as 1#, 2# and
3#. Figure 2 illustrates the experimental process. For
slab 1#, the thicknesses of HCCI and LCS were 2.5 mm
and 1 mm, respectively, and the total number of the slab
G. YUAN et al.: FABRICATION AND PROPERTIES OF HIGH-CHROMIUM CAST IRON DISPERSED STEEL ...
350 Materiali in tehnologije / Materials and technology 58 (2024) 3, 349–356
Figure 1: Microstructure of the as-cast HCCI: (a) SEM image and (b) results of the EDS analysis
Figure 2: Schematic diagram of the experiment process: a) surface treatment and assembling and b) heating and hot-rolling forming

was nine. For slab 2#, the thicknesses of HCCI and LCS
were 2.5 mm and 2 mm, respectively, and the total num-
ber of the slab was seven. For slab 3#, the thicknesses of
HCCI and LCS were 2.5 mm and 3 mm, respectively,
and the total number of the slab was seven. The LCS and
HCCI sheets were stacked in an alternating sequence.
As shown in Figure 2a, the volume ratio of HCCI in
the three types of slabs assembled was about 66.7, 48.4
and 38.5 %, respectively. The surface of the sheets was
polished mechanically and cleaned with anhydrous etha-
nol. The composite slabs were sealed by argon arc weld-
ing and then pumped by a vacuum diffusion pump to a
vacuum degree lower than1×1 0
–3
Pa. The prepared
slabs were heated in a resistance furnace, and kept at the
set temperature for 30 min before hot-rolling forming.
During the process of hot-rolling deformation, the HCCI
sheets with poor deformation performance would crack
and fracture. Thus, a composite with HCCI dispersed in
the steel matrix was prepared (Figure 2b). The compos-
ite slabs were hot-rolled at 1100 °C with a rolling rate of
0.2ms
–1
. The pass reduction was not more than 20 %. In
the forming process, multi-pass (8-9 passes) reciprocat-
ing rolling was adopted. The cumulative rolling reduc-
tions of slabs 1#, 2# and 3# were (70, 75 and 77) %, re-
spectively. The composite slabs were cooled in air after
hot rolling. Hot-rolled slabs 1#, 2# and 3# were named
CP1, CP2 and CP3, respectively.
2.3 Microstructure analysis
Specimens used for the microstructure analysis were
cut from the RD-ND section. The metallographic speci-
mens were mechanically polished and etched witha4%
nitric acid-ethanol solution. Microstructure observation
was carried out via an optical microscope (OM, Keyence
VHX-2000) and a scanning electron microscope (SEM,
SIGMA ZEISS) equipped with an energy dispersive
spectroscope (EDS).
2.4 Property tests
Specimens used for the tensile test were cut from the
middle of the sheets. The surfaces of the tensile speci-
mens were mechanically polished to remove the surface
oxide. The test specimens were processed to obtain the
size specified in GB/T228.1-2010. The tensile deforma-
tion of the specimens verified the rolling direction. Ten-
sile tests were carried out at room temperature using an
AG-100 KN tensile test machine at a speed of
1 mm/min. The digital image correlation (DIC) tech-
nique was used to measure the localized tensile strain of
the specimens. The tensile strain was analyzed based on
the change in the position of black speckles scattered
randomly on the surface of the specimen coated with
white paint.
19,20
The fracture characteristics of the tensile
specimens were observed and analyzed using the OM
and SEM.
3 RESULTS AND DISCUSSION
3.1 Macrostructure of the composite
In order to show directly the distribution structure
and shape of the two metals, the observation samples
were cut by wire cutting from the middle of the rolled
composite slab along the rolling direction. The sections
were ground, polished and etched to better distinguish
the two metals. Figure 3 shows the macroscopic mor-
phology of the RD-ND cross-sections of composites CP1
and CP3. As shown in the figure, the initial continuous
layered structure of LCS and HCCI was no longer visi-
ble. Under the influence of large cumulative deforma-
tion, the HCCI layers with poor plastic deformation abil-
ity were necked and broken into uneven blocks or
granules during rolling deformation. The fractured HCCI
was completely encased in LCS.
In composite CP1, there was a relatively high volume
of HCCI (about 66.7 %) during the forming process. Af-
ter hot-rolling forming, LCS formed a continuous
"mesh" structure, wrapping the broken HCCI. A "soft
and hard" layer net coupling structure was generated. In
this case, LCS with excellent plastic toughness can be
seen as a toughness-enhancement phase embedded in
brittle HCCI. Composite CP3 contained a relatively low
volume of HCCI (about 38.5 %) during the forming pro-
cess. After hot-rolling forming, HCCI was distributed in
LCS as granules or sheets, forming a particle-dispersed
structure. In this case, HCCI with a higher hardness can
be considered as a particle-reinforced phase embedded in
LCS.
Figure 4 displays macroscopic photographs of differ-
ent cross-sections of the composite materials. The
RD-TD cross-section of composite CP1 was revealed by
removing a 0.3 mm-thick surface layer using a grinding
machine. The RD-TD cross-sections of composites CP2
and CP3 were exposed after removing a 1.5 mm-thick
surface layer. This treatment was mainly aimed to re-
move the oxide sheet formed during hot rolling and the
thin LCS layer from the top layer. Due to its small vol-
G. YUAN et al.: FABRICATION AND PROPERTIES OF HIGH-CHROMIUM CAST IRON DISPERSED STEEL ...
Materiali in tehnologije / Materials and technology 58 (2024) 3, 349–356 351
Figure 3: Macroscopic morphology of the composite: a) morphology
of sample CP1 in the RD-ND section and b) morphology of sample
CP3 in the RD-ND section

ume in the forming process, LCS from the RD-TD sec-
tion of composite CP1 was distributed in HCCI as irreg-
ular spots or sheets. Similarly, in the RD-TD
cross-section of composite CP3 containing a small vol-
ume of HCCI, HCCI was distributed in LCS as irregular
sheets.
3.2 Microstructure of the composite
Figure 5 shows OM and SEM microstructure images
of the RD-ND cross-sections of the three types of com-
posites. Due to a serious shear deformation near the in-
terface during the forming process, the joint interface be-
tween the two metals was irregularly wavy. The necked
and fractured HCCI was wrapped by LCS. As shown in
Figure 5, some parts of the adjacent LCS layers were
bonded together. The two metal materials were well
bonded, with no delamination or large crack observed at
the bonding interface. After hot-rolling deformation, car-
bides in HCCI fractured and dissolved (Figure 5f).
Meanwhile, defects such as partial micro-cracks and car-
bide micro-holes that were not filled by the matrix were
detected in fractured carbides (indicated by red circles in
Figures 5f and 6a).
Figure 6 shows a microstructure image of the bond-
ing interface and EDS analysis results for composite
CP3. The interface of the two metals was curved and un-
dulating. A carbon-poor ferrite band was formed near the
steel side at the interface (Figure 6a). Different contents
of the elements in the two metals led to a concentration
G. YUAN et al.: FABRICATION AND PROPERTIES OF HIGH-CHROMIUM CAST IRON DISPERSED STEEL ...
352 Materiali in tehnologije / Materials and technology 58 (2024) 3, 349–356
Figure 4: Macroscopic photographs of different cross-sections of the composite materials: a), b) sample CP1; c), d) sample CP2; and e), f) sam-
ple CP3
Figure 5: Microstructures of three composites: a), b) sample CP1,
c), d) sample CP2, and e), f) sample CP3

difference at the interface. Fe, Cr, Mn and Si were dif-
fused at the interface between the two metals. Cr, Si and
Mn moved from HCCI to LCS, and Fe migrated from
LCS to HCCI. The C element was mainly distributed at
the bonding interface and in the carbides of HCCI. Ac-
cording to the line scanning analysis, the contents of Fe,
Cr, Mn and Si formed a step-like gradient distribution at
the interface, and the diffusion distance of the elements
at the interface was about 4–8 μm. A continuous diffu-
sion of the elements at the bonding interface indicated a
successful generation of a metallurgical bond.
21
3.3 Mechanical properties
The tensile properties and fracture characteristics of
the composites were analyzed. Figure 7 depicts the engi-
neering stress-strain curves of the as-cast HCCI and
composite materials. HCCI fractured directly due to brit-
tleness during the tensile process, and its elongation was
low. The overall tensile strength and elongation of the
composites were better than those of the as-cast HCCI.
The average tensile strength of composites CP1, CP2 and
CP3 was 148.2, 203.1 MPa and 223.7 MPa, respectively.
Compared with HCCI, the composites prepared had
better tensile properties, which is attributed to the addi-
tion of LCS with good strength and plasticity. The tensile
strength and elongation of the composites gradually in-
creased with the increase in the volume ratio of LCS. In
addition, it can be seen from Figure 7 that when the
stress reached the maximum, the stress-strain curve of
G. YUAN et al.: FABRICATION AND PROPERTIES OF HIGH-CHROMIUM CAST IRON DISPERSED STEEL ...
Materiali in tehnologije / Materials and technology 58 (2024) 3, 349–356 353
Figure 6: EDS analysis of the bonding interface of sample CP3: a) SEM image, b) distribution of elements, c) and d) line analysis
Figure 7: Engineering stress-strain curves of the as-cast HCCI and
composite materials

the composite materials did not terminate in a brittle
fracture, but entered a fluctuation stage.
Figure 8 describes the fracture characteristics of ten-
sile specimens CP1 and CP3. The fracture morphology
presents a curved and complex expansion process with-
out an obvious stratification. Figure 8b shows the
microstructure of fractured composite CP1. It is evident
that the two metals were closely bonded, with no crack
observed at the interface. The fracture morphology of the
LCS side is mainly dimple-shaped, indicating its good
plastic-deformation ability. There are many cleavage
planes and micro-pores formed due to carbide stripping
in the fractured HCCI, showing typical brittle fracture
characteristics.
Figure 9 displays the strain distribution along the RD
direction of composite CP3 measured with DIC at differ-
ent tensile stages. Due to the difference in the properties
of the two metals, the surface of the composite under-
went uneven deformation during the initial elastic-defor-
mation stage. With an increase in the deformation
amount, more yellow spots with a large local strain were
formed on the specimen surface (indicated by red trian-
gular arrows in Figure 9). These spots might have been
the source of cracks in brittle HCCI during the deforma-
tion process. During deformation, the material did not
fracture directly due to brittleness, but experienced a
complex process where multiple cracks were formed and
expanded. As the deformation progressed, one of the
G. YUAN et al.: FABRICATION AND PROPERTIES OF HIGH-CHROMIUM CAST IRON DISPERSED STEEL ...
354 Materiali in tehnologije / Materials and technology 58 (2024) 3, 349–356
Figure 8: Fracture characteristics of the composite materials: a), b) CP1, c), d) CP3
Figure 9: Strain distribution along the RD direction of sample CP3 at different tensile strain stages

cracks might have become the main crack and expanded
rapidly until the specimen finally broke. Different from
brittle HCCI, the bimetallic composite had a unique
three-dimensional distribution structure, which effec-
tively improved the damage tolerance and energy absorp-
tion of the composite.
4 CONCLUSIONS
In this paper, composites with HCCI distributed in
the steel matrix were prepared using the hot-rolling
forming method. The macroscopic morphology,
microstructure and mechanical properties of the compos-
ites were analyzed. The following conclusions are
drawn:
(1) The composites with HCCI distributed in the steel
matrix were successfully prepared by hot-rolling bond-
ing. The HCCI layers with poor plastic-deformation per-
formance were necked and broken into uneven blocks or
granules after hot-rolling forming. The fractured HCCI
was completely encased in LCS.
(2) After hot-rolling forming, a good metallurgical
bond was formed between the two metals. The Fe, Cr,
Mn and C elements were diffused along the interface.
(3) The tensile strength of the composites was better
than that of the as-cast iron. The average tensile strength
of composites CP1, CP2 and CP3 was 148.2, 203.1 and
223.7 MPa, respectively.
(4) The tensile fracture morphology of the compos-
ites showed a complex expansion process, and multiple
tunnel cracks were formed in brittle HCCI. The damage
tolerance and energy absorption capacity of bimetallic
composites were improved with the dispersion of HCCI
in the steel matrix.
Acknowledgments
This work was funded by the Doctoral Research
Start-Up Fund of the Anyang Institute of Technology
(No. BSJ2023003), the Henan Science and Technology
Plan Project (No. 232102230060) and the Key scientific
research projects of colleges and universities of the
Henan Province (No. 24B430003).
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